Low crystallinity glass-ceramics

ABSTRACT

Embodiments of the present disclosure pertain to crystallizable glasses and glass-ceramics that exhibit a black color and are opaque. In one or more embodiments, the crystallizable glasses and glass-ceramics include a precursor glass composition that exhibits a liquidus viscosity of greater than about 20 kPa*s. The glass-ceramics exhibit less than about 20 wt % of one or more crystalline phases, which can include a plurality of crystallites in the Fe 2 O 3 —TiO 2 —MgO system and an area fraction of less than about 15%. Exemplary compositions used in the crystallizable glasses and glass-ceramics include, in mol %, SiO 2  in the range from about 50 to about 76, Al 2 O 3  in the range from about 4 to about 25, P 2 O 5 +B 2 O 3  in the range from about 0 to about 14, R 2 O in the range from about 2 to about 20, one or more nucleating agents in the range from about 0 to about 5, and RO in the range from about 0 to about 20.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation of U.S. application Ser. No. 14/623674 filed on Feb. 17, 2015, which claims the benefit of priority under 35 U.S.C. § 119 of U.S. Provisional Application Ser. No. 61/942749 filed on Feb. 21, 2014 the content of which is relied upon and incorporated herein by reference in its entirety.

BACKGROUND

Aspects of this disclosure generally relate crystallizable glasses and glass-ceramics and processes for forming such crystallizable glasses and glass-ceramics. Specific aspects relate to crystallizable glasses exhibiting high liquidus viscosity and glass-ceramics exhibiting low crystallinity, which can be chemically strengthened.

Consumer electronic devices such as notebook computers, personal digital assistants (PDAs), portable navigation device (PNDs), media players, mobile phones, portable inventory devices (PIDs), etc. (frequently referred to as “portable computing devices”) have converged while at the same time becoming small, light, and functionally more powerful. One factor contributing to the development and availability of such smaller devices is an ability to increase computational density and operating speed by ever decreasing electronic component sizes. However, the trend to smaller, lighter, and functionally more powerful electronic devices presents a continuing challenge regarding design of some components of the portable computing devices.

Components associated with the portable computing devices encountering particular design challenges include the enclosure or housing used to house the various internal/electronic components. This design challenge generally arises from two conflicting design goals—the desirability of making the enclosure or housing lighter and thinner, and the desirability of making the enclosure or housing stronger and more rigid. Lighter enclosures or housings, typically thin plastic structures with few fasteners, tend to be more flexible while having a tendency to buckle and bow as opposed to stronger and more rigid enclosure or housings, typically thicker plastic structures with more fasteners having more weight. Unfortunately, plastics are soft materials that are easily scratched and scuffed degrading their appearance.

Among known classes of materials are glass-ceramics that are used widely in various other applications and are much harder and more scratch resistant than polymers. Glass-ceramics are used widely in appliances (e.g., cooktops, ovens, dishwashers and refrigerators), cookware, and eating utensils, such as bowls, dinner plates, and the like. Transparent glass-ceramics are used in the production of oven and/or furnace windows, optical elements, mirror substrates, and the like. Glass-ceramics are typically made by thermally treating crystallizable glass compositions at pre-specified temperatures for pre-specified periods of time to nucleate and grow crystalline phases in a glass matrix. Two glass-ceramics based on the SiO₂—Al₂O₃—Li₂O glass system comprise those having either β-quartz solid solution (β-quartz ss) as the predominant crystalline phase or β-spodumene solid solution (β-spodumene ss) as the predominant crystalline phase. These glass-ceramics are typically not formable by fusion forming techniques and, thus, have that forming limitation.

There exists a need for glass and glass-ceramic materials and technologies that provide improved choices for enclosures or housings of portable computing devices and for use in appliances.

SUMMARY

A first aspect of the present disclosure pertains to a glass-ceramic having a low crystallinity. In one or more embodiments, the glass-ceramic includes less than about 20 wt % of one or more crystalline phases. In one option, the one or more crystalline phases may include a solid solution of MgO, TiO₂, and Fe₂O₃. In another option, the one or more crystalline phases may include a plurality of crystallites in the Fe₂O₃—TiO₂—MgO system. In one or more examples, the crystallites may include MgO, Fe₂O₃, TiO₂, or combinations thereof. The crystallites may include MgO in an amount in the range from about 5 mol % to about 50 mol %, Fe₂O₃ in an amount in the range from about 15 mol % to about 65 mol %, and/or TiO₂ in an amount in the range from about 25 mol % to about 45 mol %. In some embodiments, the glass-ceramics can include TiO₂ and a ratio of TiO₂:Fe₂O₃ in the range from about 0.1 to about 3. In other embodiments, the glass-ceramics can include TiO₂ and a ratio of TiO₂:Fe₂O₃ of greater than about 2. In one example, the plurality of crystallites may include at least one of magnetite, pseudobrookite, and c-Fe₂O₃. In one or more embodiments, the plurality of crystallites forms an area fraction of about 15% or less or about 10% or less.

In some embodiments, the glass-ceramic includes one or more ϵ-Fe₂O₃ crystallites. In some cases, the ϵ-Fe₂O₃ crystallites can include Mg2+, Fe2+ ions or a combination of Mg2+ and Fe2+ ions. In other embodiments, the one or more crystalline phases present the glass-ceramics can include a solid solution of ϵ-Fe₂O₃ and MgTiO₃.

The glass-ceramics according to one or more embodiments may exhibit a black and opaque color. In one or more embodiments, the glass-ceramics may exhibit a color presented in CIELAB color space coordinates for CIE illuminant D65 determined from reflectance spectra measurements using a spectrophotometer with SCE of the following ranges: L*=from about 14 to about 30, a*=from about −1 to about +3, and b*=from about −7 to about +3.

The glass-ceramic of one or more embodiments includes a precursor glass exhibiting a liquidus viscosity of greater than about 20 kPa*s or about 50 kPa*s or greater. In some embodiments, the precursor glass is substantially transparent and exhibits an average transmission of at least about 10% in the visible-to-near-IR spectrum in the wavelength range from about 375 nm to about 1000 nm. The composition of the glass-ceramics and/or precursor glass may include, in mol %: SiO₂ in the range from about 50 to about 76, Al₂O₃ in the range from about 4 to about 25, P₂O₅+B₂O₃ in the range from about 0 to about 14, R₂O in the range from about 2 to about 20, one or more nucleating agents in the range from about 0 to about 5, and RO in the range from about 0 to about 20. Exemplary nucleating agents include TiO₂. The composition of the glass-ceramics and/or precursor glass can also include Fe₂O₃, on an oxide basis, in mol %, in an amount in the range from about 0 to about 5.

Another exemplary glass-ceramic and/or precursor glass composition may include, on an oxide basis, in mol %: SiO₂ in an amount in the range from about 58 to about 72, Al₂O₃ in an amount in the range from about 8 to about 20, B₂O₃ in an amount in the range from about 0 to about 12, R₂O in an amount in the range from about 0 to about 20, RO in an amount in the range from about 0 to about 10, SnO₂ in an amount in the range from about 0 to about 0.5, TiO₂ in an amount in the range from about 0.25 to about 5, and Fe₂O₃ in an amount in the range from about 0.25 to about 5. The composition may optionally include one or more of the following compositional relationships: R₂O—Al₂O₃ in the range from about −2 to about 3; and R_(x)O—Al₂O₃ in the range from about −2 to about 5.

Yet another exemplary glass-ceramic and/or precursor glass composition may include, on an oxide basis, in mol %: SiO₂ in an amount in the range from about 62 to about 68, Al₂O₃ in an amount in the range from about 10 to about 14, B₂O₃ in an amount in the range from about 3 to about 10, Li₂O in an amount in the range from about 0 to about 5, Na₂O in an amount in the range from about 5 to about 18, MgO in an amount in the range from about 1 to about 3, CaO in an amount in the range from about 0 to about 2, SnO₂ in an amount in the range from about 0 to about 0.2, TiO₂ in an amount in the range from about 0.25 to about 5, and Fe₂O₃ in an amount in the range from about 0.25 to about 5. The composition may optionally include one or more of the following compositional relationships: R₂O—Al₂O₃ in the range from about -1 to about 1.5; and R_(x)O—Al₂O₃ in the range from about 0 to about 2.5.

The glass-ceramics described herein also exhibit improved mechanical properties. In one or more embodiments, the glass-ceramic may be chemically strengthened (e.g., by ion exchange process(es)). Such glass-ceramics may exhibit a compressive stress of at least about 200 MPa and a depth of compressive stress layer of at least about 15 μm. In one or more embodiments, the glass ceramics exhibit an average edge strength, as measured by 4—point bend of at least about 700 MPa. In other embodiments, the glass-ceramics exhibit an average flexural strength, as measured by ring-on-ring testing, of about 2000 N or greater. In yet other embodiments, the glass-ceramics exhibit an average flexural strength, as measured by abraded ring-on-ring testing, of about 1000 N or greater.

Numerous other aspects of embodiments, embodiments, features, and advantages of this disclosure will appear from the following description and the accompanying drawings. In the description and/or the accompanying drawings, reference is made to exemplary aspects and/or embodiments of this disclosure which can be applied individually or combined in any way with each other. Such aspects of embodiments and/or embodiments do not represent the full scope of this disclosure. Reference should therefore be made to the claims herein for interpreting the full scope of this disclosure. In the interest of brevity and conciseness, any ranges of values set forth in this specification contemplate all values within the range and are to be construed as support for claims reciting any sub-ranges having endpoints which are real number values within the specified range in question. By way of a hypothetical illustrative example, a recitation in this disclosure of a range of from about 1 to 5 shall be considered to support claims to any of the following ranges: 1-5; 1-4; 1-3; 1-2; 2-5; 2-4; 2-3; 3-5; 3-4; and 4-5. Also in the interest of brevity and conciseness, it is to be understood that such terms as “is,” “are,” “includes,” “having,” “comprises,” and the like are words of convenience and are not to be construed as limiting terms and yet may encompass the terms “comprises,” “consists essentially of,” “consists of,” and the like as is appropriate.

These and other aspects, advantages, and salient features of this disclosure will become apparent from the following description, the accompanying drawings, and the appended claims.

BRIEF DESCRIPTION OF THE DRAWINGS

The drawings referenced herein form a part of the specification. Features shown in the drawings are meant to be illustrative of some, but not all, embodiments of this disclosure, unless otherwise explicitly indicated, and implications to the contrary are otherwise not to be made.

FIG. 1 shows comparisons of the transmission spectra for visible and infrared (IR) wavelengths obtained for glasses as-made and heat treated from Example Composition 15;

FIG. 2 shows the X-ray diffraction (XRD) pattern obtained for a glass-ceramic made from Example Composition 3 after heat treating at 700° C. for 4 hours;

FIG. 3 shows the XRD pattern obtained for a glass-ceramic made from Example Composition 16 after heat treating at 750° C. for 4 hours, showing the presence of pseudobrookite for which line broadening analysis suggests crystallite sizes of roughly between 15-20nm;

FIG. 4 shows the viscosity versus temperature curve denoting the liquidus temperature and viscosity for a crystallizable glass made from Example Composition 15;

FIG. 5 shows a schematic illustration of a cross section of an IX, glass-ceramic and associated characterizing parameters: compressive stress (σ_(s)) in the IX, glass-ceramic's surface layer; surface compression (CS); central tension (CT); sample thickness (t); and depth of layer (DOL) which is the perpendicular distance from the surface of the sample to the location within the sample at which the stresses changes sign {i.e., zero} resulting from surface compression and central tension) that can be determined from, for example, the sodium (Na) and/or potassium (K) concentration;

FIG. 6 shows DOL as a function of CS for glass-ceramics made according to one or more embodiments;

FIG. 7 shows an XRD pattern of a glass-ceramic made from Example Composition 3, after ceramming at 750° C. for 4 hours, an XRD pattern of a glass-ceramic made from Example Composition 10, after ceramming at 750° C. for 4 hours, an XRD pattern of a glass-ceramic made from Example Composition 17, after ceramming at 750° C. for 4 hours, and an XRD pattern of a crystallizable glass made from Example Composition 10 after annealing;

FIG. 8 shows the average dielectric constant and loss tangent as a function of R₂O—Al₂O₃ for glass-ceramics made from Example Compositions 2-7, after ceramming at 750° C. for 4 hours, over the frequency range of 400 to 3000 MHz;

FIG. 9 shows the average dielectric constant and loss tangent as a function of Fe₂O₃ content over the frequency range of 400 to 3000 MHz for glass-ceramics made from Example Compositions 9, 12 and 13, after ceramming at 700° C. for 4 hours;

FIG. 10 shows the transmission spectra of a crystallizable glass or glass-ceramic, made from Example Composition 9, having thickness of about 0.8 mm, after being subjected to various heat treatments;

FIG. 11 shows in situ transmission at various wavelengths during the ceramming process of a glass-ceramic made from Example Composition 16 through 0.5 mm path length;

FIG. 12 illustrates extinction spectra through 0.8 mm thick samples of glass-ceramics made from Example Composition 14, after ceramming at various temperatures between 700 and 850° C.;

FIG. 13 shows an Fe L23 EELS spectra of a glass-ceramic made from Example Composition 14, after ceramming at various temperatures, with an inset showing Fe3+/Total Fe ratio as a function of ceram temperature;

FIG. 14A shows a TEM micrograph of a glass-ceramic made from Example Composition 16, after ceramming at 750° C. for 4 hours;

FIG. 14B shows elemental intensity maps showing Fe, Ti and Mg enrichment and Si depletion in the crystallites of the glass-ceramic shown in FIG. 14A;

FIG. 15 shows the compositions of crystallites in Example Compositions 14 and 18 and in the glass-ceramics made from Example Compositions 14 and 18, at various ceram temperatures superimposed on the MgO—TiO₂—Fe₂O₃ 1000° C. phase diagram;

FIG. 16 is a graph illustrating the change in transmission with different compositions and ceramming temperatures;

FIG. 17 is a graph showing an XRD trace of a glass-ceramic formed from Example Composition 71, after nucleating at 630° C. for 2 hours and cerammed at 800° C. for 4 hours;

FIG. 18 is a graph showing an XRD trace of a glass-ceramic formed from Example Composition 53, after nucleating at 630° C. for 2 hours and cerammed at 775° C. for 4 hours;

FIG. 19 is a graph shown an XRD trace of a glass-ceramic formed from Example Composition 60, after nucleating at 630° C. for 2 hours and cerammed at 775° C. for 4 hours;

FIG. 20 is a FeO—Fe₂O₃—TiO₂ phase diagram showing the major solid solutions;

FIG. 21 is a HAADF STEM image and the corresponding EDS map of the different particles in a glass-ceramic formed from Example Composition 53, after nucleating at 630° C. for 2 hours and cerammed at 800° C. for 4 hours;

FIG. 22A is a graph showing the elemental composition of the crystallites of glass-ceramics made from Example Composition 53;

FIG. 22B is a graph showing the elemental composition of the crystallites of glass-ceramics made from Example Composition 71;

FIG. 23 is an electron energy-loss-near-edge-structure (ELNES) of Fe L₂₃ edge showing the change of Fe from Fe³⁺ to Fe²⁺ at different ceramming temperatures for glass-ceramics made from Example Composition 53;

FIG. 24 show HAADF STEM images of a glass-ceramic made from Example Composition 53, after being cerammed at different temperatures;

FIGS. 25A-C are graphs summarizing the image analysis of HAADF STEM images of glass-ceramics made from Example Compositions 53 and 71;

FIG. 26 illustrates the ring-on-ring (ROR) biaxial flexure load to failure of glass-ceramics made from Example Compositions 14 and 16, after ceramming at 700° C. for 4 hrs., compared to a known glass sample, before and after being ion exchanged;

FIG. 27 shows the abraded ring on ring biaxial flexure load to failure of glass-ceramics made from Example Compositions 14 and 16, after ceramming at 700° C. for 4 hrs., compared to a known glass sample, after ion exchange;

FIG. 28 shows a four point bend strength distribution of glass-ceramics made from Example Compositions 14 and 16, after ceramming at 700° C. for 4 hrs., compared to a known glass sample, before and after ion exchange;

FIG. 29 shows a FeO—TiO₂—Fe₂O₃ phase diagram;

FIG. 30 shows the average area fraction of crystallites in glass-ceramics made from Example Compositions 14 and 16, as a function of ceram temperature;

FIG. 31 shows the composition of crystallites in glass-ceramics made from Example Composition 14 as a function of ceram temperature broken down into FeO, Fe₂O₃, MgO and TiO₂ via EELS and Fe L₂₃ edge spectra;

FIG. 32 shows the characteristic failure load and strength versus ion exchanged compressive stress in a known glass sample and glass-ceramics made from Example Compositions 14 and 16, after ceramming at 700° C. for 4 hours.

DETAILED DESCRIPTION

Reference will now be made in detail to the present preferred embodiment(s), examples of which are illustrated in the accompanying drawings. While these aspects of embodiments and/or embodiments are described in sufficient detail to enable those skilled in the art to practice this disclosure, it will nevertheless be understood that no limitation of the scope of this disclosure is thereby intended. Alterations and further modifications of the features illustrated herein, and additional applications of the principles illustrated herein, which would occur to one skilled in the relevant art and having possession of this disclosure, are to be considered within the scope of this disclosure. Specifically, other aspects of embodiments and/or embodiments may be utilized, logical changes (e.g., without limitation, any one or more of chemical, compositional {e.g., without limitation, any one or more of chemicals, materials, . . . and the like}, electrical, electrochemical, electromechanical, electro-optical, mechanical, optical, physical, physiochemical, . . . and the like) and other changes may be made without departing from the spirit or scope of this disclosure.

Strong and opaque materials (often exhibiting a black color) are desirable for various applications. While known glass-ceramics have high strength and toughness, the liquidus viscosity of such materials is often too low to enable forming using fusion or slot draw methods. Alternative materials such as strengthened glasses provide high strength and scratch resistance and are transparent to visible, microwave, and radio frequency radiation; however such materials are not well suited for mobile device backs where the goal is to hide the interior workings of the device or appliance, yet allow wireless signals (e.g., cellular, WiFi, Bluetooth, etc.) to pass. Other alternative materials such as metals are tough, strong and opaque, but block wireless transmission and scratch easily. Thus, there is a need for strong, scratch resistant, opaque materials that are transparent to microwave and radio frequency radiation that are also economical to produce.

As mentioned above, strengthened glass ceramics provide good opacity and exhibit high retained strength and abraded strengths consistently above 1450 MPa, but the liquidus viscosity exhibited by these materials is often too low to enable pristine sheet formation via draw methods such as fusion or slot draw. To resolve this issue, often such materials are ground and polished after casting, pressing, or rolling, which adds additional processes steps and cost, especially for complex shapes (e.g., 3-dimensional shapes). Known glass-ceramic materials, such as β-spodumene glass-ceramics exhibit high liquidus viscosity (e.g., about 2 kPa*s), which is usually sufficient for forming by pressing, but is still an order of magnitude too low for fusion or slot drawing processes. Accordingly, the threshold liquidus viscosity for such processes is believed to about more than 20 kPa*s.

As high strength, scratch resistance and low loss in the radio and microwave portion of the spectrum were also desirable. Suitable glass-ceramics should be capable of being chemically strengthened, for example, by ion exchange processes.

To provide black, opaque materials, glass-ceramics exhibiting a crystalline phase with high absorption and low scattering across the visible are desired. Opacity is believed to be most efficiently achieved with a multiphase material so that both scattering and absorption work together to provide an intense color and the least transmission. Proper selection of the composition (i.e., of the precursor composition, crystallizable glasses and/or glass-ceramics) and oxidation states of the precipitated (or crystalline) phases in formed glass-ceramics can provide the most intense color and opacity. Moreover, to reduce scattering within the glass ceramics, which results in loss and/or change of color, the maximum allowable area fraction of the crystalline phase should be tailored. As used herein, the phrase “area fraction” means the percentage of an area of the glass-ceramic that includes crystallites. The area may be the surface area or an interior area having two-dimensions. The area size may be a minimum of about 1 inch by 1 inch.

In known materials, desirable color and opacity is often achieved empirically by changing the starting composition of the precursor composition and crystallizable glass, nucleating at 630° C. and ceramming at different temperatures in the range from about 675° C. to 850° C., without the exact knowledge regarding the composition of the crystallites in the crystalline phase, or the size and area fraction of such crystallites. It is known that if a glass is saturated in a particular phase, it can spontaneously precipitate that phase when cooled below the saturation temperature resulting in crystallization of that phase. As will be described herein, the crystallizable glasses and glass-ceramics described herein include crystallites having specific compositional limits and/or area fraction and thus exhibit desirable color and opacity. The compositions of the crystallizable glasses and glass-ceramics described herein are tailored to provide such color and opacity, as well as lower liquidus temperatures which enables a larger variety of forming options to be utilized (e.g., fusion and slot drawing).

The combination of opacity, color and high liquidus viscosity is difficult to be achieved. For black, opaque materials often include highly absorbing crystalline phases, whereas the opposite is desired for white, opaque materials. For white, opaque materials, the ideal crystalline phase exhibits minimal absorption and very high scattering. To achieve a deep rich black color, the chromophoric crystals should be as small as possible or index matched to the glass or glass phase in the glass-ceramics to prevent optical scattering, which would turn an otherwise black glass-ceramic to grey. The color intensity of the glass-ceramics can scale with the volume fraction of crystals; however, at high crystal concentrations when the crystalline components become the liquidus phase of the glass, the liquidus temperature will climb sharply causing the liquidus viscosity to plummet. Accordingly, simply increasing the area or volume fraction to achieve opacity or color can come at the expense of liquidus viscosity.

The crystallizable glasses described herein exhibit high liquidus viscosities and can be heat-treated to yield opaque, saturated black glass-ceramics with high strength. Accordingly, embodiments of the glass-ceramics described herein exhibit at least one of the following attributes: opacity, intense black color, high indentation threshold, and the capability of being formed and specifically cerammed at a high viscosity, and embodiments of the crystallizable glasses described herein exhibit at least one of the following attributes: high liquidus viscosity (e.g., greater than about 20 kPa*s) and transparency (sufficient to permit visual inspection for defects before ceramming).

Various aspects and/or embodiments of this disclosure relate to crystallizable glasses and glass-ceramics, which may be ion-exchangeable (hereinafter “IXable”) or ion-exchanged (herein after “IX”). An IXable glass or glass-ceramic refers to a glass or glass-ceramic that can be subjected to an ion exchange surface treatment. The resulting glass or glass-ceramic may be referred to as an IX glass or glass-ceramic.

In one or more embodiments, crystallizable glasses having a composition, calculated on an oxide basis in percent by mole (mol %), including:

about 50-76 SiO₂;

about 4-25 Al₂O₃;

about 0-14 P₂O₅+B₂O₃;

about 0-33 R₂O;

about 0-5 of one or more nucleating agents; and

optionally, about 0-20 RO,

may be used to form the glass-ceramics described herein. Such composition may be used in a fusion forming process to form the glass-ceramics and any intermediate glass article.

In one or more embodiments, the amount of SiO₂ in the compositions of the crystallizable glasses and/or glass-ceramics may be, in mol %, in the range from about 50 to about 76, from about 50 to about 74, from about 50 to about 72, from about 50 to about 70, from about 50 to about 68, from about 50 to about 67, from about 53 to about 76, from about 53 to about 74, from about 53 to about 72, from about 53 to about 70, from about 53 to about 68, from about 53 to about 67, from about 56 to about 76, from about 56 to about 74, from about 56 to about 72, from about 56 to about 70, from about 56 to about 68, from about 56 to about 67, from about 58 to about 76, from about 58 to about 74, from about 58 to about 72, from about 58 to about 70, from about 58 to about 68, from about 58 to about 67, from about 62 to about 76, from about 62 to about 74, from about 62 to about 72, from about 62 to about 70, from about 62 to about 68, and all ranges and sub-ranges therebetween. SiO₂ can be the main constituent of the composition and, as such, can constitute a matrix of the glass in the crystallizable glass and/or the glass-ceramic. Also, SiO₂ can serve as a viscosity enhancer for aiding in a glass's formability while at the same time imparting chemical durability to the glass. Generally, SiO₂ can be present in amounts ranging from about 50 mol % up to about 76 mol %. When SiO₂ exceeds about 76 mol %, a glass's melting temperature can be impractically high for commercial melting technologies and/or forming technologies.

In some embodiments, the amount of A1₂0₃ in the compositions of the crystallizable glasses and/or glass-ceramics may be, in mol %, in the range from about 4 to about 25, from about 4 to about 20, from about 4 to about 15, from about 4 to about 10, from about 5 to about 25, from about 5 to about 20, from about 5 to about 15, from about 5 to about 10, from about 10 to about 25, from about 10 to about 20, from about 10 to about 18, from about 10 to about 15, from about 10 to about 14 or from about 8 to about 20, and all ranges and sub-ranges therebetween. In some aspects, Al₂O₃ can be present in amounts so as to impart a resistant to devitrification to crystallizable glasses while cooling from a liquid such as, for example, from about 4 mol % to about 25 mol %. When Al₂O₃ exceeds about 25 mol %, the resultant mullite liquidus makes it difficult to melt and form crystallizable glasses while Al₂O₃ below about 4 mol % can impart an insufficient level of resistant to devitrification to crystallizable glasses while cooling from a liquid.

The embodiments described herein may include B₂O₃, which may be present, in mol %, in the range from about 0 to about 12, from about 0 to about 10, from about 0 to about 8, from about 0 to about 6, from about 0.1 to about 12, from about 0.1 to about 10, from about 0.1 to about 8, from about 0.1 to about 6, from about 1 to about 12, from about 1 to about 10, from about 1 to about 8, from about 1 to about 6, from about 3 to about 12, from about 3 to about 10, from about 3 to about 8, or from about 3 to about 6, and all ranges and sub-ranges therebetween. In one or more embodiments, the compositions of the crystallizable glasses and/or glass-ceramics described herein may include a combined amount of P₂O₅ and B₂O₃ (P₂O₅+B₂O₃), in mol %, in the range from about 0 to about 14, 0 to about 12, from about 0 to about 10, from about 0 to about 8, from about 0 to about 6, from about 3 to about 14, from about 3 to about 12, from about 3 to about 10 and all ranges and sub-ranges therebetween. P₂O₅ and B₂O₃ may be included in the compositions because, at least in part, of their capability of forming charged species in a network of such composition. The charged species can interact with other cations in a manner so as to modify one or more properties of the resultant crystallizable glasses and/or glass-ceramics. When P₂O₅+B₂O₃ exceeds about 14 mol %, any benefits resulting from their additions might not increase.

In some embodiments the total amount of R₂O in the compositions of the crystallizable glasses and/or glass-ceramics may be, in mol %, in the range from about 0 to about 33, from about 0 to about 25, from about 0 to about 20, from about 0.1 to about 33, from about 0.1 to about 25, from about 0.1 to about 20, from about 1 to about 33, from about 1 to about 25, from about 1 to about 20, from about 1, from about 4 to about 24 or from about 7 to about 20, and all ranges and sub-ranges therebetween. RO may be present in the compositions of the crystallizable glasses and/or glass-ceramics in an amount, in mol %, in the range from about 0 to about 20, from about 0 to about 15, from about 0 to about 10, from about 0 to about 8, from about 0 to about 5, from about 0.1 to about 20, from about 0.1 to about 15, from about 0.1 to about 10, from about 0.1 to about 8, or from about 0.1 to about 5 and all ranges and sub-ranges therebetween. R₂O can modify the viscosity of the composition such that a crystallizable glass exhibiting a high liquidus viscosity can be provided, while at the same time reduce the melting temperature of the crystallizable glasses and/or enable shorter thermal treatments. Also, R₂O can be used to modify viscosity of the resultant glass-ceramics. When R₂O exceeds about 33 mol %, liquidus viscosity be impractically low for commercial melting technologies and/or forming technologies.

In some embodiments, the compositions of the crystallizable glasses and/or glass-ceramics may include the following compositional criteria: R₂O+RO—Al₂O₃ in the range from about −4 to about 10, from about −2 to about 8, −2 to about 5, from about −1 to about 5, or from about 0 to about 2.5, and all ranges and sub-ranges therebetween. In other instances, the compositions of the crystallizable glasses and/or glass-ceramics may include the following composition criteria: R₂O—Al₂O₃ in the range from about −8 to about 8, from about −4 to about 4, from about −2 to about 3, from about −2 to about 2 or from about −1 to about 1.5.

In some embodiments, R₂O may include one or more of Li₂O, Na₂O, L₂O, Rb₂O, Cs₂O, Cu₂O, and Ag₂O. In one or more embodiments, Cu₂O is formed by including CuO in the batch for the crystallizable glass. In specific embodiments, R₂O may include one or more of Li₂O, Na₂O, K₂O, Rb₂O, Cs₂O, and Cu₂O. In a more specific embodiment, R₂O may include one or more of Li₂O, Na₂O, and K₂O. In an even more specific embodiment, R₂O may include one or more of Na₂O, and K₂O. Where Li₂O is utilize, it may be present in an amount, in mol %, in the range from about 0 to about 20 or from about 0 to about 5. Where Na₂O is included, it may be present in an amount, in mol %, in the range from about 0 to about 20 or from about 5 to about 18. Where K₂O is included, it may be present in an amount, in mol %, in the range from about 0 to about 10 or from about 0 to about 5.

In some embodiments, RO can include one or more of MgO, CaO, SrO, BaO, and ZnO. In one or more specific embodiments, RO can include one or more of MgO, CaO, SrO, and BaO. In even more specific embodiments, RO can include one or more of MgO, CaO, and SrO. In one or more embodiments, MgO is present in an amount, in mol %, in the range from about 0 to about 10 or from about 1 to about 3. In one or more embodiments, CaO is present in an amount, in mol %, in the range from about 0 to about 10 or from about 0 to about 2.

In one or more embodiments, the compositions of the crystallizable glass and/or glass-ceramics may also include Fe₂O₃ in an amount, in mol %, in the range from about 0.25 to about 5 or from about 0.5 to about 2. The ratio of Fe₂O₃/TiO₂ and/or Fe₂O₃/MgO may be specified. In some embodiments, the ratio may Fe₂O₃/TiO₂ may be about 2 or less, about 1.5 or less, or about 1.2 or less. In other embodiments, the ratio may Fe₂O₃/MgO may be about 2 or less, about 1.8 or less, about 1.6 or less, about 1.5 or less, or about 1.2 or less.

The compositions of the crystallizable glass and/or glass-ceramics may also include one or more nucleating agents in an amount, in mol %, in the range from about 0 to about 5, from about 1 to about 4, or from about 1 to about 3, and all ranges and sub-ranges therebetween. In some embodiments, the one or more nucleating agents may include TiO₂ and/or ZrO₂. On an oxide basis in mol %, TiO₂ can be included in the compositions of the crystallizable glass and/or glass-ceramics in an amount up to about 5, up to about 4, up to about 3 and all ranges and sub-ranges therebetween. In specific embodiments, TiO₂ may be present, in mol %, in an amount in the range from about 0.25 to about 5 or from about 0.5 to about 2. Alternatively, calculated on an oxide basis in mol %, ZrO₂ can included in the compositions of the crystallizable glass and/or glass ceramics in an amount up to about 3, or up to about 2 and all ranges and sub-ranges therebetween. When the one or more nucleating agents include TiO₂ and ZrO₂, the combined amount thereof (TiO₂+ZrO₂) can include up to about 5 mol %, up to about 4 mol %, and in some cases, the amount of ZrO₂ in the combination can be up to about 3 mol % or up to about 2 mol %, all calculated on an oxide basis. The one or more nucleation agents are incorporated to facilitate nucleation and/or growth of at least crystalline phase and any desired one or more minor crystalline phases during thermal treatment (e.g., nucleation and/or crystallization) of the crystallizable glasses described herein. When an amount of one or more nucleation agents exceeds about 5 mol %, there can be a diminishing return on the benefit of adding more. In some embodiments, the inclusion of TiO₂ as a nucleation agent is desirable when the formation of one or more Ti-containing crystalline phases is desired. In other embodiments, the inclusion of ZrO₂ as a nucleation agent can increase nucleation efficiency. In some specific embodiments, a minimum mol % sum [TiO₂+SnO₂] is in excess of 1 mole %. In some cases, effective amounts of this mol % sum [TiO₂+SnO₂] are formulated as an ingredient of crystallizable glasses so that nucleation in an effective manner occurs and growth is achieved to a preselected and appropriate crystal phase assemblage. The amount of TiO₂ above 5 mole % can be undesirable as the resultant high rutile liquidus has the potential of increasing difficulties during shape forming of crystallizable glasses and/or glass-ceramics. In some embodiments, SnO₂ may be present in an amount, in mol %, in the range from about 0 to about 0.5 or from about 0 to about 0.2.

The glass-ceramics of one or more embodiments exhibit low crystallinity. For example, the glass-ceramics may include one or more crystalline phases, which can comprise about 20 wt % or less of the glass-ceramic. In some embodiments, the crystalline phase can be about 15 wt % or less, about 10 wt % or less, or about 5 wt % or less of the glass-ceramic. In one or more embodiments, the area fraction of the crystallites may be about 20% or less, 15% or less, 10% or less or even 8% or less. In some embodiments, the area fraction may be in the range from about 0.1% to about 20%, from about 0.1% to about 18%, from about 0.1% to about 16%, from about 0.1% from about 15%, from about 0.1% to about 14%, from about 0.1% to about 13%, from about 0.1% to about 12%, from about 0.1% to about 11%, from about 0.1% to about 10%, from about 0.1% to about 9%, from about 0.1% to about 8%, from about 0.1% to about 7%, from about 0.1% to about 6%, from about 0.1% to about 5%, and all ranges and sub-ranges therebetween.

The glass-ceramics disclosed herein may include one or more oxide crystalline phases. In some embodiments, one or more silicates are substantially absent from the one or more oxide crystalline phases. Exemplary oxide crystalline phases that may be present in these glass-ceramics include one or more of TiO₂, FeO, Fe₂O₃, Fe₃O₄, MgO, FexTiyOz, FexTiyMgzOa and ZnO and, optionally, one or more transition metal oxides selected from one or more of V, Cr, Mn, Co, Ni, and Cu.

The glass-ceramics of one or more embodiments include one or more crystalline phases such as highly absorbing compounds in the Fe₂O₃—TiO₂—MgO system (e.g., magnetite, pseudobrookite, and/or ϵ-Fe₂O₃). In some embodiments, the glass-ceramics have crystallites that include MgO, Fe₂O₃, TiO₂ and/or combination thereof. Specific embodiments may include crystallites including Mg²⁺, Fe²⁺+Fe³⁺, Ti⁴⁺+ oxides and combinations thereof.

In some embodiments, the crystallites can include, in mole percent, MgO in an amount in the range from about 0 to about 60, from about 1 to about 60, from about 5 to about 60, from about 10 to about 60, from about 15 to about 60, from about 20 to about 60, from about 1 to about 55, from about 1 to about 50, from about 1 to about 45, from about 1 to about 40, from about 5 to about 50, from about 5 to about 45, from about 10 to about 40, and all ranges and sub-ranges therebetween.

In some instances, the crystallites can include, in mole percent, Fe₂O₃ in an amount in the range from about 5 to about 75, from about 5 to about 70, from about 5 to about 65, from about 5 to about 60, from about 10 to about 75, from about 15 to about 65, from about 15 to about 60, from about 15 to about 75, from about 15 to about 70, from about 15 to about 65, from about 15 to about 60, and all ranges and sub-ranges therebetween. In some instances, the crystallites can include Fe₂O₃ in an amount up to about 100 mole percent (e.g., from 40 to 100 mole percent, from 50 to 100 mole percent, or from 60 to 100 mole percent). In such embodiments, the phases can include ferrites such as magnetite (Fe₃O₄), CoFe₂O₄, MnFe₂O₄, NiFe₂O₄, and other magnetic and non-magnetic ferrites.

In other instances, the crystallites can include, in mole percent, TiO₂ in an amount in the range from about 0 to 75, 5 to 75, 10 to about75, from about 10 to about 70, from about 10 to about 65, from about 10 to about 60, from about 10 to about 55, from about 15 to about 75, from about 15 to about 70, from about 15 to about 65, from about 15 to about 60, from about 15 to about 55, from about 20 to about 75, from about 20 to about 70, from about 20 to about 65, from about 20 to about 60, from about 20 to about 55, and all ranges and sub-ranges therebetween.

In one or more embodiments, the glass-ceramics include a ϵ-Fe₂O₃ phase that exhibits extensive solid solution (ss) between Fe₂O₃ and MgTiO₃. The blackness and opacity of these ϵ-Fe₂O₃ glass-ceramics peaked at a ceram temperature of 750° C. where the Fe²⁺ in the crystallites was maximized, resulting in peak Fe²⁺—Ti⁴⁺ charge transfer absorption. The liquidus viscosity of the crystallizable glasses described herein was also increased to about 100 kPa*s or more, by optimizing the composition of the crystallizable glasses and minimizing the amount of crystallinity, thereby enabling fusion-formability. These fusion-formable crystallizable glasses and glass-ceramics also exhibited high strength properties, after being strengthened (e.g., by ion exchange processes).

In any of these embodiments, the one or more crystalline phases can include crystallites having a size of at least 5nm and less that about 300 nm, less that about 200 nm, less that about 100 nm, or less than about 50 nm, and all ranges and sub-ranges therebetween The minimum size of the crystallites may be about 5 nm or about 10 nm. As used herein, the term “size” with reference to crystallites includes the length of the longest dimension of the crystallites. In some cases, the size of the crystallites may be about 80 nm or less, about 70 nm or less, about 60 nm or less, about 50 nm or less. In some cases, the crystallites may have a size in the range from about 5 nm to about 100 nm or from about 5 nm to about 50 nm.

As described herein, some glass-ceramics are formulated to be capable of being subjected to an ion exchange treatment to provide IX glass-ceramics, which include least one surface under a compressive stress (σs) of at least about 200 MPa or at least about 700 MPa. In some embodiments, the compressively stressed surface can extend into the glass-ceramic and have a depth of layer (DOL) of at least about 1 μm, at least about 20 μm, or at least about 60 μ.m. For example, where the IX glass-ceramics have a total thickness in the range from about 0.7 millimeter (mm) up to 5 mm, the DOL may be in the range from about 20 μm to about 150 μm, from about 30 μm to about 120 μm, from about 40 μm to about 100 μm. In specific instances, the total thickness of the IX glass-ceramics may be in the range from about 0.7 mm to about 2 mm, or from about 0.7 mm to 1.3 mm. In some embodiments, the glass-ceramics disclosed herein are subjected to ion exchange treatment to impart antimicrobial properties to the glass-ceramics and/or IX glass-ceramics described herein. In such embodiments, the glass-ceramics and/or IX glass-ceramics are immersed in a bath including antimicrobial components such as AgNO₃, and/or a Cu-containing salt such as CuCl/CuSO₄ and/or aqueous CuCl. A mixture of CuCl and KCl, a mixture of CuCl and NaCl, and/or a mixture of all three of CuCl, KCl and NaCl may also be utilized for a Cu-containing salt bath.

The IX glass-ceramics according to one or more embodiments, which have been subjected to an ion exchange treatment, exhibit a Vickers median crack initiation threshold of at least 5 kilograms force (kgf), at least 10 kgf, at least 15 kgf, or at least 20 kgf, and all range and sub-ranges therebetween. In one or more embodiments, the crystallizable glasses and/or glass-ceramics described herein exhibit high strength. For example, in some embodiments, the crystallizable glasses and/or glass-ceramics exhibit a flexural strength, as measured by ring on ring (ROR), in the range from about 2000 N to about 4000 N, from about 2000 N to about 3800 N, from about 2000 N to about 3600 N, from about 2000 N to about 3400 N, from about 2000 N to about 3200 N, from about 2000 to about 3000 N, from about 2100 N to about 3000 N, from about 2200 N to about 3000 N, from about 2300 N to about 3000 N, from about 2400 N to about 3000N, from about 2500 N to about 3000 N, from about 2600 N to about 3000 N, from about 2700 N to about 3000 N, from about 2750 N to about 3000 N, from about 2800 N to about 3000 N, from about 2850 N to about 3000 N, from about 2900 N to about 3000 N, and all ranges and sub-ranges therebetween. In specific embodiments, the crystallizable glasses and/or glass-ceramics exhibit a flexural strength, as measured by ring on ring (ROR), in the range from about 200 kgf to about 400 kgf break load. In even more specific embodiments, the crystallizable glasses and/or glass-ceramics exhibit a flexural strength, as measured by ring on ring (ROR), in the range from about 200 kgf to about 380 kgf, from about 200 kgf to about 360 kgf, from about 200 kgf to about 340 kgf, from about 200 kgf to about 320 kgf, from about 200 kgf to about 300 kgf, from about 210 kgf to about 400 kgf, from about 220 kgf to about 400 kgf, from about 230 kgf to about 400 kgf, from about 240 kgf to about 400 kgf, from about 250 kgf to about 400 kgf, from about 260 kgf to about 400 kgf, or from about 270 kgf to about 400 kgf break load, and all ranges and sub-ranges therebetween.

In one or more embodiments, the crystallizable glasses and/or glass-ceramics exhibit a flexural strength, as measured by abraded ring on ring (aROR) and after being abraded with about 1 ml of SiC particles at 34kPa pressure, in the range from about 700 N to about 1500 N, from about 750 N to about 1500 N, from about 800 N to about 1500 N, from about 850 N to about 1500 N, from about 900 N to about 1500 N, from about 950 N to about 1500 N, from about 1000 to about 1500 N, from about 900 N to about 1450 N, from about 900 N to about 1400 N, from about 900 N to about 1350 N, from about 900 N to about 1300 N, from about 900 N to about 1250 N, from about 900 N to about 1200 N, from about 900 N to about 1150 N, from about 900 N to about 1100, and all ranges and sub-ranges therebetween. In other embodiments, the crystallizable glasses and/or glass-ceramics exhibit a flexural strength, as measured by abraded ring on ring (aROR) and after being abraded with about 1 ml of SiC particles at 34 kPa pressure, in the range from about 100 kgf to about 200 kgf, from about 100 kgf to about 190 kgf, from about 100 kgf to about 180 kgf, from about 100 kgf to about 170 kgf, from about 100 kgf to about 160 kgf, from about 100 kgf to about 150 kgf, from about 110 kgf to about 200 kgf, from about 120 kgf to about 200 kgf, from about 130 kgf to about 200 kgf, from about 140 kgf to about 200 kgf, and all ranges and sub-ranges therebetween.

In one or more embodiments, the crystallizable glasses and/or glass-ceramics exhibit an edge strength, as measured by 4 point bend, in the range from about 600 MPa to about 1000 MPa, from about 600 MPa to about 950 MPa, from about 600 MPa to about 900 MPa, from about 600 MPa to about 850 MPa, from about 600 MPa to about 800 MPa, from about 600 MPa to about 750 MPa, from about 600 MPa to about 700 MPa, from about 650 MPa to about 1000 MPa, from about 700 MPa to about 1000 MPa, from about 750 MPa to about 1000 MPa, from about 800 MPa to about 1000 MPa, and all ranges and sub-ranges therebetween.

In one or more embodiments, the glass-ceramics, whether IX or not, exhibit a color presented in CIELAB color space coordinates for CIE illuminant D65 determined from reflectance spectra measurements using a spectrophotometer with SCE with an a* coordinate from about −2 to about +8 and a b* coordinate from about −7 to about +20. In some embodiments, the a* coordinate exhibited by the glass-ceramics may be from about −3 to about +3, from about −2 to about +3, from about −1 to about +3, from about −2 to about +2 or from about −1 to about +1. The b* coordinate exhibited by the glass-ceramics may be from about −10 to about +10, from about −8 to about +8, from about −7 to about +7, from about −6 to about +6, from about −5 to about +5, from about −4 to about +4, from about −3 to about +3, from about −2 to about +3, from about −2 to about +2, from about −1 to about +1 and all ranges and sub-ranges therebetween. In some embodiments, the glass-ceramics may exhibit a L* coordinate that can approach dark colors and/or black while in other of these aspects the L* coordinate can approach light colors and/or white. For example for dark colors and/or black, presented in CIELAB color space coordinates for CIE illuminant D65 determined from reflectance spectra measurements using a spectrophotometer with SCE, the glass-ceramics may exhibit a L* coordinate from about 0 to about 30, from about 5 to about 30, from about 10 to about 30, from about 12 to about 30, from about 14 to about 30, from about 16 to about 30, from about 0 to about 20, from about 0 to about 15, from about 0 to about 10, from about 0 to about 5, or from about 0 to about 3.

The glass-ceramics described herein may also exhibit an average %transmission of at least one wavelength, λ_(T), in an interval of wavelengths from about 390 nm to about 1000 nm of less than about 50, less than about 40, less than about 30, less than about 20 or less than about 10. In some embodiments, the % transmission of at least one wavelength, 4, in an interval of wavelengths from about 390 nm-2000 nm or from about 390 nm-1000 nm, may be less than about 5, less than about 4, less than about 3, less than about 2, less than about 1 and about 0. Alternatively, various glass-ceramic embodiments can have an average value in percent (%) of transmission over a λ interval from about 390 nm to about 1000 nm

$\left\lbrack {{\begin{matrix} {2500\mspace{14mu} {nm}} \\ {390\mspace{14mu} {nm}} \end{matrix}{T_{avg}(\%)}} = {\frac{1}{\left( {2500 - {390\mspace{14mu} {nm}}} \right)}{\sum\limits_{390\mspace{14mu} {nm}}^{2500\mspace{14mu} {nm}}{T_{\lambda}\left\{ \% \right\}}}}} \right\rbrack$

of less than about 50, less than about 40, less than about 30, less than about 20 or less than about 10. Over wavelengths from about 200 nm to about 780 nm, the transmission of some embodiments may be less than about 10%, or less than about 5%. In some instances, over a 100 nm wavelength segment along the wavelength range from about 200nm to about 780nm, the average transmission may be less than about 5%, less than 1%, or less than 0.1%. Such average % transmissions recited herein may be exhibited by glass-ceramics having a thickness of about 0.8mm.

The glass-ceramics disclosed herein may exhibit certain dielectric properties. That is, in addition to such glass-ceramics having one or more preselected colors, which additionally might be tunable or have been tuned, for example, to impart one or more aesthetic colors, such glass-ceramics can possess advantageous dielectric properties. In one or more embodiments, the glass-ceramics may exhibit a loss tangent over a frequency ranging from about 0.5-3.0 GHz at about 25° C. and/or a dielectric constant over a frequency ranging from about 0.5-3.0 GHz at about 25° C.

Exemplary glass-ceramics may be formulated to be capable of being formed from a molten state using one or more of a float method, a slot draw method, and/or a fusion method and, optionally, subsequently a redraw method and/or roll out method. To that end, in some embodiments, crystallizable glasses have compositions formulated to form the glass-ceramics exhibit a liquidus viscosity (η_(lqds)) of at least about 20 kP, at least about 50 kP, at least about 100 kP, or at least about 150 kP, and all ranges and sub-ranges therebetween. In some embodiments, the liquidus viscosity of the composition may be in the range from about 20 kP to about 100000 kP, from about 50 kP to about 100000 kP, or from about 1000 kP to about100000 kP. In some other aspects, such compositions are formulated to exhibit a liquidus temperature (T_(lqds)) of less than about 1600° C., less than about 1400° C., less than about 1300° C., less than about 1200° C. or even less than about 1100° C., less than about 1000, less than about 900C. In some embodiments, the compositions are formulated to exhibit a T_(lqds) of about 650° C. or greater.

The crystallizable glass compositions described herein may be formulated for ease of processing (e.g., melting, processing, forming . . . etc.). In such embodiments, the crystallizable glasses may exhibit an average %transmission of at least one wavelength, λ_(T), in an interval of wavelengths from about 390 nm-2000 nm or from about 390 nm-1000 nm, of least about 90, at least about 70 or at least about 50. The crystallizable glasses of some embodiments may exhibit an average value in percent (%) of transmission over a λ interval from about 390 nm to about 1000 nm

$\left\lbrack {{\begin{matrix} {2500\mspace{14mu} {nm}} \\ {390\mspace{14mu} {nm}} \end{matrix}{T_{avg}(\%)}} = {\frac{1}{\left( {2500 - {390\mspace{14mu} {nm}}} \right)}{\sum\limits_{390\mspace{14mu} {nm}}^{2500\mspace{14mu} {nm}}{T_{\lambda}\left\{ \% \right\}}}}} \right\rbrack$

of at least about 40, of at least about 50, at least about 70, or at least about 90. Such average % transmissions recited herein may be exhibited by crystallizable glasses having a thickness of about 0.8 mm. Over a wavelength range from about 390 nm to about 780 nm, the transmission of some embodiments is about 30% or greater, or up to 90%. In some instances, over a 100 nm wavelength segment along the wavelength range from about 200 nm to about 780 nm, the average transmission is greater than 30%, greater than 70%, or up to about 90%.

The crystallizable glasses of one or more embodiments, may be formulated to be crystallizable at one or more preselected temperatures for one or more preselected times to a glass-ceramic, such as those described herein. Accordingly, in some specific embodiments, the crystallizable glasses may exhibit a viscosity (η) at which crystals are grown, of at least about 10E¹⁰P, at least about 10E⁹P, or at least about 10E⁸P.

In one or more embodiments, the crystallizable glass may have specific optical properties. For example, the crystallizable glasses may be transparent or substantially transparent. In some cases, the crystallizable glasses may exhibit an average transmission of at least about 10% or at least about 50% in the visible-to-near-IR spectrum in the wavelength range from about 375 nm to about 2000 nm. In some cases, the average transmission can be as high as 60%, 70% or even 80%.

The crystallizable glasses described herein may optionally include one or more colorants. The amount of the colorants can vary and can include, up to about 5.2 mol %, up to about 4 mol %, up to about 2.8 mol %, or up to about 1.5 mol % of the crystallizable glass, calculated on an oxide basis.

The one or more colorants can be formulated to provide one or more Fe²⁺ sources, one or more Fe³⁺ sources and/or the combination of Fe²⁺ and Fe³⁺ sources to the crystallizable glasses and/or resulting glass-ceramics formed from the crystallizable glasses. In other embodiments, such one or more colorants can be formulated to provide one or more iron oxides and one or more other transition metal oxides to crystallizable glasses and/or resulting glass-ceramics formed therefrom. In still other embodiments, such one or more one or more colorants can be, for example, one or more of TiO₂, FeO, Fe₂O₃, Fe₃O₄, MgO, and ZnO and, optionally, one or more transition metal oxides selected from one or more of V, Cr, Mn, Co, Ni, and Cu. The one or more other transition metal oxides can be an oxide of one or more of Ti, Mn, Co, and Cu,. In still other embodiments, the one or more one or more colorants can be formulated to provide one or more multivalent metal oxides and, optionally, one or more reducing agents to crystallizable glasses and/or progeny glass-ceramics. In such embodiments, the one or more multivalent metal oxides can include an oxide of one or more of Ti, Mn, Fe, Co, Cu. In each of these embodiments, one or more silicates may be substantially absent from the one or more oxide crystalline phases.

In some embodiments, Fe and/or Sn may be included as part of a fining package during glass formation. Where a Sn-free glass is desired, Fe may be used in the fining package.

Another aspect of this disclosure pertains to process(es) for making the crystallizable glasses and glass-ceramics described herein. The processes include providing such crystallizable glasses and glass-ceramics that exhibit one or more preselected colors. In some embodiments, raw materials for making crystallizable glasses and progeny glass-ceramics can be formulated to provide these preselected color(s)s that can be tunable or have been tuned.

In other embodiments, the processes for making the crystallizable glasses and/or glass-ceramics described herein including formulating the crystallizable glasses in such manner to facilitate processing using mechanized means, including continuous, semi-continuous, and/or batch-wise processing in a manufacture of shaped parts of the crystallizable glasses and glass-ceramics described herein. Non-limiting examples of shaped parts can range from sheets or fibers to one or more complex three dimensional (3D) shapes such as, for example, a concave shape, a convex shape, or any other desired predetermined geometry . . . etc. For example in the case of sheets, one or more crystallizable glass sheets can be formed from a molten state by any one of a float method or a down draw methods, such as a slot draw method or a fusion method. If desirable, such crystallizable glass sheets might be then subjected to one or more redraw methods and/or one or more roll out methods. Such one or more redraw methods and/or one or more roll out methods might be performed while the crystallizable glass sheets are in a viscous state between about 10E^(3.5)P to 10E^(7.6)P.

In one or more embodiments, the crystallizable glasses and glass-ceramics described herein may be formed using any one of a float process, a fusion down-draw process, a slot-draw process, or any other suitable process typically used for forming crystallizable glasses substrates from a batch of glass raw materials. As a specific example, the crystallizable glasses described herein might be formed into glass substrates using a fusion down-draw process. Such fusion down-draw processes utilize a drawing tank that has a channel for accepting molten glass raw material. The channel has weirs that open at the top along the length of the channel on both sides of the channel. When the channel fills with molten glass, the molten glass overflows the weirs and, due to gravity, the molten glass flows down the outside surfaces of the drawing tank as two flowing glass surfaces. These outside surfaces extend downwardly and inwardly while joining at an edge below the drawing tank. The two flowing glass surfaces join at this edge and fuse to form a single flowing sheet of molten glass that may be further drawn to a desired thickness. The fusion down-draw process produces glass sheets with highly uniform, flat surfaces as neither surface of the resulting glass sheet is in contact with any part of the fusion apparatus.

In some embodiments, the liquidus viscosity of the crystallizable glass may be tuned to enable use of a fusion down-draw process in forming the glasses described herein. The liquidus viscosity may be modified to limit or minimize the crystal growth in the glass during formation.

As an alternative specific example, the one or more crystallizable glasses of this disclosure and described herein may be formed using a slot-draw process in which molten glass raw materials are supplied to a drawing tank. The bottom of the drawing tank has an open slot with a nozzle that extends the length of the slot. The molten glass flows through the slot/nozzle and is drawn downward as a continuous sheet and into an annealing region.

The molten glass raw materials are formulated to produce the crystallizable glasses described herein upon fining and homogenization of the molten glass compositions at a temperature between about 1400° C. and about 1650° C.

In one or more embodiments, the processes for making the glass-ceramics described herein includes heat treating the crystallizable glasses at one or more preselected temperatures for one or more preselected times to induce crystallization (i.e., nucleation and growth) of one or more crystalline phases (e.g., having one or more compositions, amounts, morphologies, sizes or size distributions, etc.). In one or more specific embodiments, the heat treatment can include (i) heating crystallizable glasses at a rate of 1-10° C./min to a nucleation temperature (Tn) in the range from about 600° C. to about 750° C. (e.g., 630° C.); (ii) maintaining the crystallizable glasses at the nucleation temperature for a time in the range from between about ¼ hr to about 4 hr to produce nucleated crystallizable glasses; (iii) heating the nucleated crystallizable glasses at a rate in the range from about 1° C./min to about 10° C./min to a crystallization temperature (Tc) in the range from about 575° C. to about 900° C. (e.g., from about 700° C. to about 775° C.); (iv) maintaining the nucleated crystallizable glasses at the crystallization temperature for a time in the range from about ¼ hr to about 4 hr to produce the glass-ceramics described herein; and (v) cooling the formed glass-ceramics to room temperature. As used herein, the term crystallization temperature may be used interchangeably with ceram or ceramming temperature. In addition, the terms “ceram” or “ceramming” may be used to refer to steps (iii), (iv) and optionally (v), collectively.

Temperature-temporal profile of heat treatment steps (iii) and (iv), in addition to crystallizable glass compositions, are judiciously prescribed so as to produce one or more of the following desired attributes: crystalline phase(s) of the glass-ceramics, proportions of one or more predominate crystalline phases and/or one or more minor crystalline phases and residual glass, crystal phase assemblages of one or more predominate crystalline phases and/or one or more minor crystalline phases and residual glass, and grain sizes or grain size distributions among one or more predominate crystalline phases and/or one or more minor crystalline phases, which in turn may influence the final integrity, quality, color, and/or opacity, of resultant formed glass-ceramics.

The resultant glass-ceramic sheets can then be reformed by pressing, blowing, bending, sagging, vacuum forming, or other means into curved or bent pieces of uniform thickness. Reforming can be done before thermally treating or the forming step can also serve as a thermal treatment step where both forming and thermally treating are performed substantially simultaneously. For example a crystallizable glass might be formed into a 3D shape by forming the crystallizable glass into tubing and thermally treating the 3D crystallizable glass to transforming it into black, 3D glass-ceramic tubing. In some embodiments, the forming might precede the transforming, or the transforming might precede the forming, or the transforming might occur substantially simultaneously with the forming.

In yet other embodiments, the compositions used to form the crystallizable glasses and/or glass-ceramics can be formulated, for example, so that the glass-ceramics described herein are capable of being transformed to IX glass-ceramics using one or more ion exchange techniques. In these embodiments, ion exchange can occur by subjecting one or more surfaces of such glass-ceramics to one or more ion exchange baths, having a specific composition and temperature, for a specified time period to impart to the one or more surfaces with compressive stress(es) (σs). The compressive stresses can include one or more average surface compressive stress (CS), and/or one or more depths of compressive stresses (which may be referred to as one or more depths of layer (DOL)).

The bath(s) used in the ion exchange process represent an ion source having one or more ions having an ionic radius larger than the ionic radius of one or more ions present in the glass-ceramic (and, more particularly, the ions present in at least one surface of the glass-ceramic). During immersion of the glass-ceramic into the bath, the ions in the glass-ceramic having smaller radii can replace or be exchanged with ions having larger radii. This exchange may be facilitated or achieved by controlling the bath and/or glass-ceramic temperature within a range of temperatures at which ion inter-diffusion (e.g., the mobility of the ions from between bath and the glass-ceramic) is sufficiently rapid within a reasonable time (e.g., between about 1 hr. and 64 hrs. or from 4-16 hrs., ranging at between about 300° C. and 500° C. or from 400° C.-430° C.). Also, typically such temperature is below the glass transition temperature (Tg) of any glass of a glass-ceramic. Some exemplary ions that may be exchanged between the bath and the glass-ceramic include sodium (Na⁺), lithium (Li⁺), potassium (K⁺), rubidium (Rb⁺), and/or cesium (Cs⁺) ions. In one scenario, the bath may include sodium (Na⁺), potassium (K⁺), rubidium (Rb⁺), and/or cesium (Cs⁺) ions, which may be exchanged for lithium (Li⁺) ions in the glass-ceramic. Alternatively, ions of potassium (K⁺), rubidium (Rb⁺), and/or cesium (Cs⁺) in the bath can be exchanged for sodium (Na⁺) ions in the glass-ceramic. In another scenario, ions of rubidium (Rb⁺) and/or cesium (Cs⁺) in the bath may be exchanged for potassium (K⁺) ions in the glass-ceramics.

Some examples of ion sources include one or more gaseous ion sources, one or more liquid ion sources, and/or one or more solid ion sources. Among one or more liquid ion sources are liquid and liquid solutions, such as, for example molten salts. For example for the above ion-exchange examples, such molten salts can be one or more alkali metal salts such as, but not limited to, one or more halides, carbonates, chlorates, nitrates, sulfites, sulfates, or combinations of two or more of the proceeding. In one example, suitable alkali metal salts can include potassium nitrate (KNO₃), sodium nitrate (NaNO₃) and the combination thereof. It should be noted that in addition to single step IX processes, multiple step IX processes can be utilized to provide a specific CS to the surface of the glass-ceramic and thus, enhance a glass-ceramic's performance. In some embodiments, single step IX processes can be accomplished by exchanging ion (particularly lithium-for-sodium ion exchange) into a surface of the glass-ceramic by placing a glass-ceramic article in NaNO₃ baths at between about 300° C. and 500° C. for between about lhr and 64 hr. In other embodiments, single step IX processes can be accomplished by placing a glass-ceramic article in a mixed potassium/sodium baths at (e.g. a 80/20 KNO₃/NaNO₃ bath, a 60/40 KNO₃/NaNO₃ bath, or even a 50/50 KNO₃/NaNO₃ bath . . . etc.) at between about 300° C. and 500° C. for between about 1 hr and 64 hr. In still other embodiments, two-step IX process can be accomplished by first placing a glass-ceramic article in a Li-containing salt bath (e.g. the molten salt bath can be a high temperature sulfate salt bath composed of Li₂SO₄ as a major ingredient, but diluted with Na₂SO₄, K₂SO₄ or Cs₂SO₄ in sufficient concentration to create a molten bath) between about 300° C. and 500° C. for between about 1 hr and 64 hr followed by placing the IX, glass-ceramic in a Na-containing salt bath between about 300° C. and 500° C. for between about 1 hr and 64 hr. The first step of the two step IX process functions to replace the larger sodium ions in the in the glass-ceramic's at least one surface with the smaller lithium ions found in the Li-containing salt bath. The second step of the two step IX process functions to exchange Na into in the glass-ceramic's at least one surface.

In a more particular embodiment, the glass-ceramics may have to a thickness (e.g., in the range from about 0.7 mm up to about 5 mm, from about 0.7 mm to about 2 mm, or from about 0.7 mm to about 1.3 mm) and compressive layer having an average surface compressive stress of about 500 MPa or greater and a DOL of about 40 μm or greater.

Various articles may incorporate or utilize the crystallizable glasses and/or glass-ceramics described herein. For example, covers and/or housings used in electronic devices might be formed using the crystallizable glasses and/or glass-ceramics. In still yet other embodiments, the crystallizable glasses and glass-ceramics might be used in a variety of electronic devices or portable computing devices, which might be configured for wireless communication, such as, computers and computer accessories, such as, “mice”, keyboards, monitors (e.g., liquid crystal display (LCD), which might be any of cold cathode fluorescent lights (CCFLs-backlit LCD), light emitting diode (LED-backlit LCD) . . . etc., plasma display panel (PDP) . . . and the like), game controllers, tablets, thumb drives, external drives, whiteboards . . . etc.; personal digital assistants (PDAs); portable navigation device (PNDs); portable inventory devices (PIDs); entertainment devices and/or centers, devices and/or center accessories such as, tuners, media players (e.g., record, cassette, disc, solid-state . . . etc.), cable and/or satellite receivers, keyboards, monitors (e.g., liquid crystal display (LCD), which might be any of cold cathode fluorescent lights (CCFLs-backlit LCD), light emitting diode (LED-backlit LCD) . . . etc, plasma display panel (PDP) . . . and the like), game controllers . . . etc.; electronic reader devices or e-readers; mobile or smart phones . . . etc. As alternative examples, the crystallizable glasses and glass-ceramics might be used in automotive applications (e.g., consoles, automotive body parts and panels), appliances, architectural applications (e.g., sinks, faucets, shower walls, bathtubs, outlet covers, countertops, backsplashes, elevator cabs etc.), and energy production applications (e.g., solar thermal parts).

In one or more embodiments, the glass-ceramics described herein may be incorporated into a display, and specifically as a cover for a display. In some embodiments, such glass-ceramics may be semi-opaque (i.e., have an average transmittance in the range from about 0.1% to about 25% over a wavelength range about 200 nm to about 780 nm). In such embodiments, the glass-ceramic provides a display cover that hides the light emitting devices in the display (such as TFT displays, and backlit LED buttons and icons) when they such light emitting devices are not in operation (i.e., the semi-opaque display cover appears completely opaque), thereby providing a surface that does not appear to be a display (i.e., forming a “dead front”). When the light emitting devices are in operation, the light emitting therefrom are transmitted through the semi-opaque display cover. In one or more embodiments, such displays may be incorporated into countertops, cabinet doors, refrigerator doors, appliance surfaces, automotive interiors, and the like. In one or more embodiments, the display cover can be touch-enabled, and thus be used to input information. Such embodiments may include projected capacitive (pCAP) TFT displays, button pCAP systems and the like.

The use of glass-ceramics described herein as display covers provides an improvement over neutral density filters, which typically use thick glass materials (which may not be not suitable for high sensitivity touch operation or for low parallax effects), or plastic (which does not provide a durable surface). The use of glass-ceramics described here as display covers also provides an improvement over semi-mirrored films that are typically metallic-based and thus interfere with the electric field of the projective capacitance touch panels resulting in little or no touch sensitivity. Moreover, the semi-mirrored films provide a reflective surface when the light emitting devices are not in operation, which may be undesirable. The use of glass-ceramics described herein as display covers also provides an improvement over electrochromic material such as tungsten oxide and viologens (which change color when a charge is applied and some materials can be made to transition from “clear” to some known, repeatable dark or light state) as such electrochromic materials can be costly and require the use of electrodes and electrical connections that may negatively influence the projective capacitive touch sensors. Finally, the use of glass-ceramics described herein as display covers provides an advantage over the use of micro-holes in a visually textured material, which can weaken the mechanical integrity of the surface, and requires a bright display to provide a sufficiently bright image to the viewer. Moreover, micro-holes are currently only believed to be feasible with stainless steel materials and thus, different colors may not be achievable using this method.

Identity of phase assemblages and/or crystalline sizes for the crystallizable glasses and glass-ceramics described herein was determined or could be determined by XRD analysis techniques known to those in the art, using such commercially available equipment as the model as a PW1830 (Cu Kα radiation) diffractometer manufactured by Philips, Netherlands. Spectra were typically acquired for 2θ from 5 to 80 degrees.

Elemental profiles measured for characterizing the surfaces of the crystallizable glasses and/or glass-ceramics described herein were determined or could be determined by analytical techniques know to those in the art, such as, electron microprobe (EMP); x-ray photoluminescence spectroscopy (XPS); secondary ion mass spectroscopy (SIMS) . . . etc.

Compressive stress (σ_(s)) in a surface layer, average surface compression (CS), and depth of layer (DOL) of the crystallizable glasses can be conveniently measured using conventional optical techniques and instrumentation such as commercially available surface stress meter models FSM-30, FSM-60, FSM-6000LE, FSM-7000H . . . etc. available from Luceo Co., Ltd. and/or Orihara Industrial Co., Ltd., both in Tokyo, Japan. Glass-ceramics can also be measured in a similar manner using infrared light sources.

During an IX processes as discussed above, ions having a smaller ionic radius present in the glass-ceramic surface and/or bulk can be exchanged with ions having a larger ionic radius. As schematically illustrated in FIG. 5, when this results in compressive stress (σ_(s)) in the surface 110 of a sample 100, balancing tensile stresses are induced in a central region 130 of the sample 100 to balance the forces throughout the sample 100. The CS is related to the central tension (CT) by the following relationship:

CS=CT×(t−2DOL)/DOL;

where t is the thickness of the glass-ceramic sample 100 and

-   -   DOL (depth of layer 120) is the distance from the surface 110 of         the sample 100 along a normal to the surface 110 to the location         at which the stresses within the sample 100 change sign (i.e.,         zero).

For a sample 100, the integrated central tension (ICT) is given by the integral of stress throughout the tensile portion of the stress profile (i.e., central region 130 of the sample 100). ICT is related to the full thickness (t) of the sample 100, the depth of layer (DOL) 120 of the compressive stress layer, the average central tension (CT), and the shape or profile of the compressive stress layer by the following relationship:

ICT=CT×(t−2DOL),

where the thickness (t-2DOL) of the central region 130 is a direction perpendicular to the surface. To balance forces within the sample 100, the integrated surface compression (ICS) has the same magnitude as the ICT, but has an opposite (minus) sign, since the overall integrated stress of the sample must be zero: −ICS +ICT=0. ICS is related to the DOL 120 of the compressive stress layer, the CS, and the shape or profile of the compressive stress layer by the following relationship: ICS=CS×DOL, where the DOL of the compressive stress region has be defined above (i.e., the distance from the surface 110 of the sample 100 along a normal to the surface 110 to the location at which the stresses within the sample 100 change sign (i.e., zero)).

Vickers indentation cracking threshold measurements were performed or could be performed on the crystallizable glasses and/or glass-ceramics described herein to identify the threshold at which cracks initiate in a surface of such materials. The measurements were performed using known techniques such as, for example, in pages 130-132 of “Materials Science and Engineering (third edition)” by William D. Callister (John Wiley & Sons, New York, 1994), which are incorporated by reference herein. Unless otherwise specified, the Vickers indentation cracking threshold measurements described herein are performed by applying and then removing an indentation load using a Vickers indenter (a=68.00°) to a glass surface at 0.2 mm/min. The indentation maximum load is held for 10 seconds. The indentation cracking threshold is defined as the indentation load at which greater than 50% of 10 indents exhibit any number of radial/median cracks emanating from the corners of the indent impression. The maximum load is increased until such threshold is met for a given glass composition. Vickers indentation cracking threshold measurements are performed at room temperature in 50% relative humidity.

Flexural strength of the crystallizable glasses and/or glass-ceramics described herein was and/or can be characterized by methods know to those in the art, such as, those described in ASTM C1499. Young's Modulus, Shear Modulus, and Poisson's Ratio of the crystallizable glasses and/or glass-ceramics described herein were and can be characterized by methods know to those in the art, such as, those described in ASTM C1259. Knoop hardness and Vickers hardness of crystallizable glasses and/or glass-ceramics described herein was and/or can be characterized by methods know to those in the art, such as, those described in ASTM C1326 and ASTM C1327, respectively.

EXAMPLES

The following examples illustrate the various embodiments of this disclosure and in are no way intended to limit this disclosure thereto.

Inasmuch as the sum of the individual constituents totals or very closely approximates 100, for all practical purposes the reported values may be deemed to represent weight percent (wt %). The actual crystallizable glass batch ingredients may comprise any materials, either oxides, or other compounds, which, when melted together with the other batch components, will be converted into the desired oxide in the proper proportions.

Example Compositions 1-115: The Example Compositions listed in Tables I, Ia, Ib and Ic were used to form crystallizable glasses by introducing appropriately batched raw materials to a platinum crucible. The crucible was then placed in a furnace having a temperature up to about 1700° C. The materials were then refined and the molten glasses were then either poured onto a steel plate to make patties of glass, or they were formed into sheet by rolling or down draw.

In particular, crystallizable glasses formed from Example Compositions 1-7, 14-17 and 43-44 were melted by mixing 2500g of batched raw materials in a 1.81 platinum crucible, which was then placed in a SiC globar furnace having a temperature of about 1600° C. for 5 hours. The melted materials were then poured a thin stream into a bucket of flowing cold water to make cullet. The cullet was then remelted at 1650° C. for 5 hours to obtain a homogeneous melt and then poured onto a steel table and subsequently annealed for 2 hours at about 620° C.

Example Composition 1 was formulated to evaluate the effect of high Fe₂O₃ content in the composition on opacity and color. Example Compositions 2-6 were formulated to examine the effect of excess alkali relative to Al₂O₃ (Na₂O+K₂O—Al₂O₃) at lower Fe₂O₃ level. This was done to address spontaneous crystallization and improve liquidus viscosity. Example Compositions 7, 14-17 and 43-44 incorporated different levels of TiO₂, MgO, and Fe₂O₃ to avoid magnetite, and improve the liquidus viscosity. The compositions from Example Compositions 1-7, 14-17 and 43-44that exhibited acceptable liquidus viscosities and high opacity after ceramming, were then tuned to provide Example Compositions 53, 57, 60, 63 and 71, which were made into thin sheets (having a thickness in the range from about 1 mm to about 3 mm) on an electrically fired gas assisted continuous melting unit. The glass sheets made from Example Compositions 53, 57, 60, 63 and 71 were not annealed.

TABLE I Glass Composition Mole Percent (Mol %) R₂O + TiO₂ Ex. SiO₂ Al₂O₃ B₂O₃ P₂O₅ Na₂O MgO CaO SnO₂ TiO₂ ZrO₂ Fe₂O₃ Co₃O₄ MnO₂ R₂O—Al₂O₃ RO—Al₂O₃ Fe₂O₃ 1 63.37 13.65 5.01 0 13.48 2.33 0 0 0 0 2.16 0 0 −0.18 2.16 0 2 64.64 12.84 5.11 0 14.84 0.70 0 0.08 0 0 1.8 0 0 2.00 2.70 0 3 64.64 13.34 5.11 0 14.34 0.70 0 0.08 0 0 1.8 0 0 1.00 1.70 0 4 64.64 13.84 5.11 0 13.84 0.70 0 0.08 0 0 1.8 0 0 0.00 0.70 0 5 64.64 14.34 5.11 0 13.34 0.70 0 0.08 0 0 1.8 0 0 −1.00 −0.30 0 6 64.64 14.84 5.11 0 12.84 0.70 0 0.08 0 0 1.8 0 0 −2.00 −1.30 0 7 62.64 13.84 5.11 0 13.84 0.70 0 0.08 2 0 1.8 0 0 0.00 0.70 1.11 8 65.22 14.97 5.16 0 12.95 0.71 0 0.08 0 0 0.91 0 0 −2.02 −1.31 0 9 65.03 14.93 5.14 0 12.91 0.70 0 0.08 0 0 1.21 0 0 −2.01 −1.31 0 10 64.83 14.88 5.12 0 12.88 0.70 0 0.08 0 0 1.50 0 0 −2.01 −1.30 0 11 63.02 13.92 5.14 0 13.92 0.70 0 0.08 2.01 0 1.21 0 0 0.00 0.70 1.67 12 61.00 14.93 5.14 0 12.91 0.70 0 0.08 4.02 0 1.21 0 0 −2.01 −1.31 3.33 13 58.99 14.93 5.14 0 12.91 0.70 0 0.08 6.04 0 1.21 0 0 −2.01 −1.31 5 14 62.64 13.93 5.11 0 13.75 2 0 0.08 2 0 0.5 0 0 −0.18 1.82 4 15 63.64 13.93 5.11 0 13.75 1.75 0 0.08 1 0 0.75 0 0 −0.18 1.57 1.33 16 62.64 13.93 5.11 0 13.75 1.75 0 0.08 2 0 0.75 0 0 −0.18 1.57 2.67 17 61.64 13.93 5.11 0 13.75 1.75 0 0.08 3 0 0.75 0 0 −0.18 1.57 4 18 63.64 13.93 5.11 0 13.75 1.50 0 0.08 1 0 1 0 0 −0.18 1.32 1 19 63.64 13.93 5.11 0 13.75 1.25 0 0.08 1 0 1.25 0 0 −0.18 1.07 0.80 20 64.70 14.85 5.11 0 12.75 2 0 0.08 0 0 0.5 0 0 −2.10 −0.10 0 21 64.70 14.85 5.11 0 12.75 1.75 0 0.08 0 0 0.75 0 0 −2.10 −0.35 0 22 64.70 14.85 5.11 0 12.75 1.50 0 0.08 0 0 1.00 0 0 −2.10 −0.60 0 23 64.54 14.81 5.10 0 12.72 1.75 0 0.08 0 0 0.75 0.25 0 −2.10 −0.35 0 24 64.38 14.78 5.09 0 12.69 1.74 0 0.08 0 0 0.75 0.5 0 −2.09 −0.35 0 25 63.20 14.85 5.11 0 12.75 1.75 0 0.08 1.50 0 0.75 0 0 −2.10 −0.35 2 26 63.11 14.03 5.15 0 13.85 1.01 0 0.08 2.01 0 0.76 0 0 −0.18 0.83 2.67 27 62.79 13.96 5.12 0 13.78 1.50 0 0.08 2.00 0 0.75 0 0 −0.18 1.32 2.67 28 62.48 13.89 5.10 0 13.71 1.99 0 0.08 1.99 0 0.75 0 0 −0.18 1.82 2.67 29 62.64 13.43 5.11 0 14.25 1.75 0 0.08 2 0 0.75 0 0 0.82 2.57 2.67 30 62.64 14.43 5.11 0 13.25 1.75 0 0.08 2 0 0.75 0 0 −1.18 0.57 2.67 31 59.80 14.95 0.00 4.98 14.95 2.49 0 0.08 1.99 0 0.75 0 0 0.00 2.49 2.67 32 63.50 13.83 5.46 0 13.65 1.74 0 0.08 0.99 0 0.74 0 0 −0.18 1.56 1.33 33 64.20 13.25 5.12 0 13.75 1.75 0 0.08 1.1 0 0.75 0 0 0.50 2.25 1.47 34 63.64 13.93 5.11 0 13.75 1.75 0 0.08 1 0 0.75 0 0 −0.18 1.57 1.33 35 61.75 13.43 5.11 0 14.25 2.38 0 0.08 0 0 3 0 0 0.82 3.20 0 36 61.75 13.93 5.11 0 13.75 2.38 0 0.08 0 0 3 0 0 −0.18 2.20 0 37 61.75 14.43 5.11 0 13.25 2.38 0 0.08 0 0 3 0 0 −1.18 1.20 0 38 62.75 13.93 5.11 0 13.75 2.38 0 0.08 0 0 2 0 0 −0.18 2.20 0 39 60.75 13.93 5.11 0 13.75 2.38 0 0.08 0 0 4 0 0 −0.18 2.20 0 40 63.75 13.93 5.11 0 13.75 2.38 0 0.08 0 1 0 0 0 −0.18 2.20 — 41 63.64 13.93 5.11 0 13.75 1.75 0 0.08 1 0 0.75 0 0 −0.18 1.57 1.33 42 64.62 13.44 5.11 0 13.24 1.75 0 0.08 1 0 0.75 0 0 −0.20 1.55 1.33 43 64.05 13.93 5.11 0 13.75 1.75 0 0.08 0.83 0 0.50 0 0 −0.18 1.57 1.66 44 63.78 13.93 5.11 0 13.75 1.75 0 0.08 1 0 0.60 0 0 −0.18 1.57 1.67 45 63.51 13.93 5.11 0 13.75 1.75 0 0.08 1.17 0 0.70 0 0 −0.18 1.57 1.67 46 63.65 13.90 5.10 0 13.72 1.75 0 0.08 1 0 0.60 0 0.2 −0.18 1.57 1.67 47 63.53 13.87 5.09 0 13.70 1.74 0 0.08 1 0 0.60 0 0.4 −0.18 1.56 1.67 48 64.18 13.93 5.11 0 13.75 1.75 0 0.08 0 0 0.60 0 0.6 −0.18 1.57 0 R₂O + TiO₂ Ex. SiO₂ Al₂O₃ B₂O₃ P₂O₅ Na₂O K₂O MgO CaO SnO₂ TiO₂ ZrO₂ Fe₂O₃ Co₃O₄ MnO₂ R₂O—Al₂O₃ RO—Al₂O₃ Fe₂O₃ 49 63.77 13.92 5.12 0 13.71 0.01 1.92 0.04 0.09 0.98 0.02 0.42 0 0 −0.19 1.78 2.34 51 63.74 13.96 5.12 0 13.69 0.01 1.75 0.03 0.12 1.00 0.03 0.55 0 0.01 −0.25 1.53 1.8 52 63.79 13.92 5.12 0 13.66 0.01 1.74 0.04 0.12 0.98 0.03 0.56 0 0 −0.25 1.53 1.74 53 63.82 13.89 5.10 0 13.76 0.01 1.74 0.03 0.06 0.98 0.03 0.56 0 0 −0.11 1.67 1.73 54 53.71 13.83 5.08 0 13.76 0.02 1.75 0.03 0.05 0.98 0.03 0.56 0 0.19 −0.06 1.91 1.73 55 63.77 13.96 5.08 0 13.56 0.02 1.75 0.04 0.06 0.99 0.03 0.57 0 0.19 −0.39 1.4 1.74 56 63.81 13.83 5.08 0 13.61 0.01 1.75 0.03 0.05 1.2 0.03 0.57 0 0.02 −0.21 1.59 2.12 57 63.81 13.69 5.11 0 13.60 0.02 1.74 0.03 0.05 1.35 0.03 0.56 0 0.01 −0.07 1.71 2.41 58 63.83 13.66 5.13 0 13.62 0.02 1.76 0.03 0.05 1.24 0.03 0.63 0 0.01 −0.03 1.77 1.98 59 63.96 13.61 5.17 0 13.63 0.01 1.75 0.03 0.06 1.00 0.06 0.71 0 0.01 0.03 1.82 1.42 60 63.94 13.60 5.18 0 13.66 0.01 1.75 0.03 0.06 0.99 0.06 0.71 0 0.01 0.08 1.87 1.40 61 64.05 13.6 5.17 0 13.77 0.01 1.43 0.03 0.05 0.98 0.06 0.74 0 0.11 0.18 1.64 1.33 62 64.23 13.58 5.19 0 13.70 0.02 1.22 0.03 0.05 0.98 0.07 0.75 0 0.19 0.14 1.58 1.30 63 65.08 13.19 4.97 0 13018 0.01 1.73 0.03 0.03 0.98 0.04 0.75 0 0.01 0 1.77 1.32 64 65.06 13.13 5.03 0 13.22 0.01 1.75 0.03 0.02 0.98 0.02 0.74 0 0.01 0.1 1.89 1.32 65 64.91 13.13 5.15 0 13.11 0.01 1.73 0.03 0.02 0.97 0.02 0.63 0.26 0.01 0 1.77 1.54 66 65.16 13.31 4.85 0 12.16 0.95 1.74 0.04 0.02 0.99 0.02 0.75 0.01 0.01 −0.2 1.58 1.32 67 65.46 12.95 4.50 0 13.04 0.39 1.54 0.03 0.02 1.30 0.01 0.74 0.01 0.01 0.48 2.06 1.76 68 66.00 12.70 3.74 0 13.60 0.04 1.62 0.03 0.02 1.47 0.01 0.76 0.01 0.01 0.94 2.6 1.93 69 65.97 12.77 3.68 0 13.62 0.02 1.41 0.03 0.02 1.49 0.01 0.76 0.01 0.22 0.87 2.52 1.95 70 65.96 12.70 3.71 0 12.79 0.88 1.61 0.03 0.02 1.50 0.01 0.76 0.01 0.03 0.97 2.63 1.96 71 66.13 12.73 3.69 0 13.17 0.55 1.63 0.03 0.02 1.32 0.01 0.68 0.01 0.03 0.99 2.67 1.95

TABLE Ia Glass Composition Mole Percent (Mol %) R₂O + TiO₂ Ex. SiO₂ Al₂O₃ P₂O₅ Na₂O K₂O MgO CaO SrO BaO ZnO La₂O₃ Ta₂O₅ SnO₂ TiO₂ Fe₂O₃ R₂O—Al₂O₃ RO—Al₂O₃ Fe₂O₃ 72 60.15 14.98 5 14.98 0 2.49 0.06 0 0 0 0 0 0.08 1.50 0.75 0 2.56 2 74 60.89 14.99 4.99 14.98 0 2.51 0.06 0 0 0 0 0 0.08 0.75 0.75 0 2.57 1 75 61.14 14.98 5 14.98 0 2.51 0.06 0 0 0 0 0 0.08 0.5 0.75 0 2.57 0.67 76 60.42 14.98 4.99 14.98 0 2.49 0.06 0 0 0 0 0 0.08 2 0.00 0 2.55 — 78 60.30 15.02 5.01 15.01 0 2.50 0.06 0 0 0 0 0 0.08 1.50 0.50 −0.01 2.56 2.99 79 60.23 15.01 5 15.00 0 2.51 0.06 0 0 0 0 0 0.08 1.51 0.60 −0.01 2.56 2.50 80 60.00 14.95 4.98 14.95 0 2.48 0.06 0 0 0 0 0 0.08 1.50 1.00 0 2.55 1.50 81 60.30 15.02 5.01 15.03 0 2.01 0.05 0 0 0 0 0 0.08 1.50 1.00 0 2.07 1.50 82 60.91 15.18 5.06 15.18 0 1.02 0.05 0 0 0 0 0 0.08 1.51 1.01 0 1.08 1.50 83 60.37 14.99 5 14.99 0 2.49 0.06 0 0 0 0 0 0.08 0 2 0 2.56 0 84 57.08 15.56 7.55 15.09 0.47 0.38 3.78 0 0 0 0 0 0.08 0 0 0.01 4.16 0 86 55.01 15.00 10.91 14.55 0.46 0.36 3.64 0 0 0 0 0 0.08 0 0 0.01 4.00 0 87 56.02 15.28 11.11 14.81 0.46 0.38 1.85 0 0 0 0 0 0.08 0 0 0 2.23 0 90 57.07 15.57 8.49 15.11 0.47 0.38 2.83 0 0 0 0 0 0.07 0 0 0.01 3.23 — 91 57.08 15.57 8.49 15.11 0.47 0.37 0.00 0 0 2.83 0 0 0.07 0 0 0.01 3.21 — 92 57.09 15.57 8.49 15.09 0.47 0.37 0.00 2.83 0 0 0 0 0.07 0 0 −0.01 3.19 — 93 57.08 15.57 8.49 15.10 0.47 0.38 0.00 0 2.83 0 0 0 0.08 0 0 0 3.22 — 94 57.07 15.57 8.49 15.10 0.48 0.38 0.00 0 0 0 2.83 0 0.08 0 0 0.01 0.39 — 95 57.10 15.57 8.49 15.09 0.47 0.38 0.00 0 0 0 0 2.83 0.07 0 0 −0.01 0.37 — 96 56.02 15.27 5.56 14.83 0.47 0.38 3.70 0 0 0 0 0 0.08 3.71 0 0.02 4.09 — 97 55.02 15.00 7.28 14.54 0.45 0.36 3.63 0 0 0 0 0 0.07 3.63 0 −0.01 3.99 — 98 54.03 14.74 8.93 14.29 0.44 0.35 3.57 0 0 0 0 0 0.07 3.57 0 0 3.92 — 99 56.04 15.28 7.41 14.81 0.46 0.37 1.85 0 0 0 0 0 0.07 3.70 0 −0.01 2.21 — 100 55.00 14.55 7.27 15.00 0.46 0.36 3.64 0 0 0 0 0 0.07 3.63 0 0.91 4.91 — 101 55.01 15.46 7.27 14.09 0.45 0.36 3.64 0 0 0 0 0 0.07 3.63 0 −0.92 3.09 — 102 59.91 16.34 5.94 15.84 0.50 0.39 0.99 0 0 0 0 0 0.08 0 0 0 1.38 — 103 59.33 16.18 5.88 15.69 0.49 0.39 1.97 0 0 0 0 0 0.08 0 0 0 2.36 — 104 58.17 15.87 5.77 15.39 0.48 0.39 3.85 0 0 0 0 0 0.08 0 0 0 4.24 — 105 58.18 15.87 7.69 15.39 0.48 0.38 1.92 0 0 0 0 0 0.08 0 0 0 2.31 — 106 59.32 15.69 5.89 16.18 0.49 0.39 1.96 0 0 0 0 0 0.08 0 0 0.98 3.33 — 107 59.32 16.67 5.88 15.21 0.49 0.39 1.96 0 0 0 0 0 0.08 0 0 −0.97 1.38 —

TABLE Ib Glass Composition Mole Percent (Mol %) R₂O + TiO₂ Ex. SiO₂ Al₂O₃ B₂O₃ Na₂O MgO TiO₂ Fe₂O₃ CuO Cu2O R₂O—Al₂O₃ RO—Al₂O₃ Fe₂O₃ 108 65 13.2 5 13.3 1.75 1 0.75 0 0 0.1 1.85 1.33 109 65 13.2 5 13.2 1.75 1 0.75 0.2 0 0 1.95 1.33 110 65 13.2 5 12.3 1.75 1 0.75 2 0 −0.9 2.85 1.33 111 65 13.2 5 8.3 1.75 1 0.75 10 0 −4.9 6.85 1.33 112 65 13.2 5 8.3 1.75 1 0.75 0 5 0.1 1.85 1.33 113 65 13.2 5 13.3 1.75 0 0 0.2 0 0.1 2.8 0

TABLE Ic Glass Composition Mole Percent (Mol %) R₂O + TiO₂ Ex. SiO₂ Al₂O₃ B₂O₃ Na₂O K₂O MgO CaO SnO2 ZrO2 TiO2 Fe2O3 MnO CoO R₂O—Al₂O₃ RO—Al₂O₃ Fe₂O₃ 114 63.803 13.989 5.098 13.655 0.014 1.747 0.034 0.060 0.028 0.986 0.581 0.00 0.00 −0.320 1.461 1.697 115 64.919 13.189 5.060 13.163 0.014 1.751 0.031 0.020 0.020 0.983 0.677 0.00 0.17 −0.011 1.771 1.452

TABLE II Glass Properties Heat Treated Glass Strain Annealing Softening α P T_(lqds) LiqVisc Liquidus PB Crystal Ex. Point (° C.) Point (° C.) Point (° C.) (10⁻⁷/° C.) (g/cm³) (° C.) (kP) Phase(s) As Made 700° C.-4 hr 750° C.-4 hr 800° C.-4 hr Size (nm) 1 559 608 888 76.1 2.46 1235 12.2 Mag Mag Mag Mag 2 Mag Amorph Amorph Amorph 3 1050 402 <1050° C. Amorph Mag Mag 4 Hem + Ma Amorph Mag Mag 5 Hem + Ma Mag Mag Mag 6 Hem + Ma Mag + Hem Mag + Hem Mag 7 PB Mag Mag + PB Mag + PB 8 Amorph Amorph Amorph 9 Amorph Mag + Hem Mag + Hem 10 Amorph Mag Mag 11 Mag + possibly Mag + PB another phase 12 PB + possibly PB another phase 13 PB + Rutile PB + Rutile 14 566 617 900 2.43 1110 116 Amorph PB PB 15 560 612 883 2.42 1050 493 Amorph ε-Fe₂O₃ ε-Fe₂O₃ 16 563 613 891 2.43 1140 60 Amorph Mag + PB PB 17 566 619 904 2.45 1155 <45 Amorph PB PB 18 556 607 880 2.43 Amorph Mag Mag + PB 19 559 609 893 2.43 Amorph Mag Mag + possibly another phase 20 21 22 23 24 25 26 574 626 2.43 1120 PB PB 18 27 572 626 2.43 1110 trace Mag PB 17 18 570 623 2.44 1105 PB PB 17 29 559 608 2.44 1085 PB PB 20 30 575 627 2.43 1135 PB PB 15 31 625 680 2.45 1065 658 32 1045 470 33 1050 34 1065 35 36 37 38 39 40 41 2.42 1095 216 42 2.42 1070 422 43 1065 Amorph ε-Fe₂O₃ ε-Fe₂O₃ 44 1070 Amorph ε-Fe₂O₃ ε-Fe₂O₃ 45 1100 46 1060 47 1065 48 1030 Glass Properties Strain Pt. Annealing Softening α P Beta- T_(lqds) (° C.)-24 hrs T_(lqds) (° C.)-72 hrs LiqVisc (Kp)-24 hr LiqVisc (Kp)-72 hr HTV Ex. (° C.) Pt. (° C.) Pt. (° C.) (10⁻⁷/° C.) (g/cm³) OH Air Int. Pt. Air Int. Pt. Air Int. Pt. Air Int. Pt. A B To 49 1070 1065 1080 −3.6 9581.7 30.1 51 567 619 2.409 0.405 −3.5 9092.2 59.7 52 53 2.407 1075 1025 1040 335 1010 1040 335 967 696 274 1358 696 −3.5 9256.3 40.0 54 55 1075 1035 1055 311 311 726 471 56 565 617 881.9 74.1 2.408 0.391 −3.4 8983.9 57.7 57 1095 1045 1085 181 181 496 220 58 −3.9 10198.7 −32.1 59 −3.5 9403.4 41.9 60 562 613 2.353 0.373 1100 1035 1075 170 170 637 277 −3.2 8610.6 86.9 61 559 611 74.7 2.412 0.365 −3.8 10189.2 −12.7 62 1125 1075 1040 90 90 224 448 −3.5 9439.9 31.6 63 1120 1050 1055 150 1055 1075 150 604 544 125 544 359 −3.3 9104.4 53.6 64 1025 1050 136 950 549 −3.5 9573.9 29.4 65 1020 1015 208 1066 1191 −3.4 9383.4 33.6 66 1045 1110 132 692 190 −3.3 9156.8 45.9 67 1045 1090 159 702 280 −3.9 10646.2 −46.7 68 1125 1150 62 161 103 69 567 617 2.418 0.358 1040 1085 183 811 323 −3.3 8945.3 54.1 70 1050 1075 138 650 391 −3.9 10557.8 −43.7 71 1015 1015 1040 1349 1349 793 −3.6 9581.7 30.1 Glass Properties Heat Treated Glass Ex. T200 P T16 kP T35 kP T160 kP 700° C.-4 hr 750° C.-4 hr 800° C.-4 hr PB Crystal Size (nm) 49 51 52 53 1641 1251 1200 1113 ε-Fe₂O₃ ε-Fe₂O₃ ε-Fe₂O₃ 54 55 1637 1246 1195 1109 56 57 1632 1239 1189 1102 PB PB 58 59 60 1637 1241 1190 1103 ε-Fe₂O₃ 61 62 1623 1232 1181 1093 63 1650 1255 1204 1116 ε-Fe₂O₃ ε-Fe₂O₃ 64 1652 1250 1199 1111 65 1647 1254 1203 1114 66 1666 1261 1209 1119 67 1669 1261 1209 1120 68 1671 1267 1215 1125 69 1675 1265 1213 1122 70 1679 1265 1212 1122 71 1671 1267 1214 1123 ε-Fe₂O₃ ε-Fe₂O₃ PB + ε-Fe₂O₃ Glass Properties Heat Treated Glass Ex. Annealing Pt (° C.) P (g/cm³) T_(lqds) (° C.) Color (850° C.-4 hr) XRD (750° C.-4 hr) XRD (780° C.-4 hr) XRD (800° C.-4 hr) XRD (850° C.-4 hr) 72 700 Brown Rutile, PB, Hematite 74 700 Amber translucent Amorphous 75 700 Amber translucent Amorphous 76 700 White GC Anatase 78 680 Khaki Grey translucent Trace Berlinite, Magnetite Trace Rutile Rutile 79 680 Khaki Grey translucent Trace Berlinite, Magnetite Rutile Rutile 80 680 Black Opaque PB, Berlinite, Magnetite PB, Rutile PB, Rutile 81 680 1080 Black Opaque PB, Berlinite, Magnetite PB, Rutile PB, Rutile 82 680 1090 Black Opaque PB, Berlinite, Magnetite PB, Rutile PB, Rutile 83 680 Black Opaque Magnetite or Magnetite or Magnetite or Magnesioferrite Magnesioferrite Magnesioferrite 84 680 White Light Opal 86 680 White Opal 87 680 Clear Glass Amorphous Amorphous Amorphous Amorphous 90 680 White Opal 91 680 Clear Glass 92 680 White Opal 93 680 Clear Glass 94 680 Spontaneous Ceramic 95 680 Clear Glass 96 680 Bluish White Light Opal 97 680 White GC 98 680 Cream Opal 99 680 White GC 100 680 White GC 101 680 White Opal 102 680 103 680 104 680 105 680 106 680 107 680

TABLE III Example-> 49 51 52 53 XRD Results As Made Glass amorphous Heat Treated Glasses Nucleation Growth Temperature-time Temperature- (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs 630° C.-2 hrs 725° C.-4 hrs Amorphous 630° C.-2 hrs 750° C.-4 hrs ε-Fe₂O₃ 630° C.-2 hrs 775° C.-4 hrs ε-Fe₂O₃ 630° C.-2 hrs 800° C.-4 hrs ε-Fe₂O₃ Indentation Threshold (kg) As Made Glass-> 37.5 Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs 50 630° C.-2 hrs 700° C.-4 hrs 22.5 630° C.-2 hrs 725° C.-4 hrs 630° C.-2 hrs 750° C.-4 hrs Transmission Percent (%) As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs 13.22 27.98 630° C.-2 hrs 700° C.-4 hrs 83.49 0.98 0.97 630° C.-2 hrs 725° C.-4 hrs 0.07 na 630° C.-2 hrs 750° C.-4 hrs 0.08 0.05 630° C.-2 hrs 775° C.-4 hrs 4 630° C.-2 hrs 800° C.-4 hrs na Example−> 54 55 56 57 58 XRD Results As Made Glass Heat Treated Glasses Nucleation Growth Temperature-time Temperature- (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs 630° C.-2 hrs 725° C.-4 hrs ε-Fe₂O₃ 630° C.-2 hrs 750° C.-4 hrs ε-Fe₂O₃ PB ε-Fe₂O₃ 630° C.-2 hrs 775° C.-4 hrs ε-Fe₂O₃ PB 630° C.-2 hrs 800° C.-4 hrs ε-Fe₂O₃ Indentation Threshold (kg) As Made Glass-> 37.5 Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs 22.5 630° C.-2 hrs 700° C.-4 hrs 630° C.-2 hrs 725° C.-4 hrs 630° C.-2 hrs 750° C.-4 hrs Transmission Percent (%) As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs 3.71 0.06 0.07 0.08 630° C.-2 hrs 700° C.-4 hrs 0.08 0.16 0.06 0.08 0.06 630° C.-2 hrs 725° C.-4 hrs 0.09 0.08 0.11 0.09 630° C.-2 hrs 750° C.-4 hrs 0.04 0.04 0.15 0.63 0.08 630° C.-2 hrs 775° C.-4 hrs 0.13 0.95 630° C.-2 hrs 800° C.-4 hrs Example-> 59 60 61 62 63 XRD Results As Made Glass Amorphous Amorphous Heat Treated Glasses Nucleation Growth Temperature-time Temperature- (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs ε-Fe₂O₃ ε-Fe₂O₃ 630° C.-2 hrs 725° C.-4 hrs ε-Fe₂O₃ Trace Magnetite 630° C.-2 hrs 750° C.-4 hrs ε-Fe₂O₃ ε-Fe₂O₃ ε-Fe₂O₃ ε-Fe₂O₃ 630° C.-2 hrs 775° C.-4 hrs ε-Fe₂O₃ ε-Fe₂O₃ ε-Fe₂O₃ 630° C.-2 hrs 800° C.-4 hrs Indentation Threshold (kg) As Made Glass-> Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs 630° C.-2 hrs 725° C.-4 hrs 630° C.-2 hrs 750° C.-4 hrs Transmission Percent (%) As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-T_(c) 630° C.-2 hrs 675° C.-4 hrs 0.06 630° C.-2 hrs 700° C.-4 hrs 0.07 0.86 0.08 0.03 630° C.-2 hrs 725° C.-4 hrs 0.05 0.03 0.07 0.04 0.03 630° C.-2 hrs 750° C.-4 hrs 0.07 0.02 0.07 0.03 630° C.-2 hrs 775° C.-4 hrs 0.03 0.05 630° C.-2 hrs 800° C.-4 hrs Example-> 64 65 66 67 68 XRD Results As Made Glass Heat Treated Glasses Nucleation Growth Temperature-time Temperature- (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs 630° C.-2 hrs 725° C.-4 hrs 630° C.-2 hrs 750° C.-4 hrs PB 630° C.-2 hrs 775° C.-4 hrs PB 630° C.-2 hrs 800° C.-4 hrs Indentation Threshold (kg) As Made Glass-> Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs 17.5 630° C.-2 hrs 725° C.-4 hrs 630° C.-2 hrs 750° C.-4 hrs Transmission Percent (%) As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs 0.09 0.04 0.02 0.05 630° C.-2 hrs 700° C.-4 hrs 0.09 0.03 0.02 0.03 630° C.-2 hrs 725° C.-4 hrs 0.02 0.03 0.05 0.02 0.02 630° C.-2 hrs 750° C.-4 hrs 0.03 0.02 0.03 0.03 0.03 630° C.-2 hrs 775° C.-4 hrs 0.03 0.02 0.05 0.92 1.35 630° C.-2 hrs 800° C.-4 hrs Example-> 69 70 71 XRD Results As Made Glass Amorphous Heat Treated Glasses Nucleation Growth Temperature-time Temperature- (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs 630° C.-2 hrs 725° C.-4 hrs 630° C.-2 hrs 750° C.-4 hrs 630° C.-2 hrs 775° C.-4 hrs 630° C.-2 hrs 800° C.-4 hrs Indentation Threshold (kg) As Made Glass-> 35-40 Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs 630° C.-2 hrs 700° C.-4 hrs 37.5 630° C.-2 hrs 725° C.-4 hrs 630° C.-2 hrs 750° C.-4 hrs Transmission Percent (%) As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs 0.02 0.03 0.02 630° C.-2 hrs 700° C.-4 hrs 0.02 0.03 0.02 630° C.-2 hrs 725° C.-4 hrs 0.02 0.03 0.03 630° C.-2 hrs 750° C.-4 hrs 0.04 0.04 0.04 630° C.-2 hrs 775° C.-4 hrs 0.4  0.97 0.25 630° C.-2 hrs 800° C.-4 hrs

TABLE IV Example-> 49 51 52 53 CIE L* D65 SCE Results As Made Glass Heat Treated Glasses Nucleation Growth Temperature- Temperature- time (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 0.54 2.78 630° C.-2 hrs 700° C.-4 hrs 64.69 0.28 0.25 630° C.-2 hrs 725° C.-4 hrs 0.93 0.6 630° C.-2 hrs 750° C.-4 hrs 3.2 5.67 630° C.-2 hrs 775° C.-4 hrs 17.085 10.21 630° C.-2 hrs 800° C.-4 hrs 26.76 CIE a* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs 0.62 7.09 630° C.-2 hrs 700° C.-4 hrs 2.6 0.05 0.03 630° C.-2 hrs 725° C.-4 hrs −0.1 0.08 630° C.-2 hrs 750° C.-4 hrs −0.3 −0.135 630° C.-2 hrs 775° C.-4 hrs −1.15 −0.54 630° C.-2 hrs 800° C.-4 hrs −1.29 CIE b* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs −0.14 3.59 630° C.-2 hrs 700° C.-4 hrs 28.68 −0.31 −0.35 630° C.-2 hrs 725° C.-4 hrs −1.46 −0.95 630° C.-2 hrs 750° C.-4 hrs −3.75 −4.89 630° C.-2 hrs 775° C.-4 hrs −6.265 −6.06 630° C.-2 hrs 800° C.-4 hrs −2.82 Example-> 54 55 56 57 58 CIE L* D65 SCE Results As Made Glass Heat Treated Glasses Nucleation Growth Temperature- Temperature- time (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 0.39 0.26 0.19 0.41 630° C.-2 hrs 700° C.-4 hrs 0.345 0.27 0.27 0.2 630° C.-2 hrs 725° C.-4 hrs 1.14 0.29 0.22 0.19 630° C.-2 hrs 750° C.-4 hrs 2.08 0.29 0.34 0.35 630° C.-2 hrs 775° C.-4 hrs 0.99 1.28 630° C.-2 hrs 800° C.-4 hrs CIE a* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs −0.03 0.03 0.01 0.04 630° C.-2 hrs 700° C.-4 hrs 0.005 −0.08 0 −0.01 630° C.-2 hrs 725° C.-4his −0.12 −0.15 −0.04 0.04 630° C.-2 hrs 750° C.-4 hrs −0.21 0.07 −0.06 −0.06 630° C.-2 hrs 775° C.-4 hrs −0.09 −0.09 630° C.-2 hrs 800° C.-4 hrs CIE b* D65 SCE Results As Made Glass-> Heat Treated Glasses Tt-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs −0.48 −0.41 −0.25 −0.53 630° C.-2 hrs 700° C.-4 hrs −0.74 −0.34 −0.36 −0.26 630° C.-2 hrs 725° C.-4 hrs −1.62 −0.36 −0.29 −0.3 630° C.-2 hrs 750° C.-4 hrs −2.53 −0.41 −0.55 −0.44 630° C.-2 hrs 775° C.-4 hrs −1.25 −1.89 630° C.-2 hrs 800° C.-4 hrs Example-> 59 60 61 62 63 CIE L* D65 SCE Results As Made Glass Heat Treated Glasses Nucleation Growth Temperature- Temperature- time (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 0.24 630° C.-2 hrs 700° C.-4 hrs 0.17 0.45 0.33 0.18 630° C.-2 hrs 725° C.-4 hrs 0.5 0.23 0.26 0.2 0.12 630° C.-2 hrs 750° C.-4 hrs 0.7 1.37 0.77 0.45 630° C.-2 hrs 775° C.-4 hrs 1.09 0.56 630° C.-2 hrs 800° C.-4 hrs CIE a* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs −0.01 630° C.-2 hrs 700° C.-4 hrs 0.02 0.11 0.02 −0.05 630° C.-2 hrs 725° C.-4 hrs −0.01 0.03 −0.01 0.065 0.03 630° C.-2 hrs 750° C.-4 hrs −0.05 0.15 −0.07 0.02 630° C.-2 hrs 775° C.-4 hrs 0.07 −0.05 630° C.-2 hrs 800° C.-4 hrs CIE b* D65 SCE Results As Made Glass-> Heat Treated Glasses Tt-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs −0.42 630° C.-2 hrs 700° C.-4 hrs −0.28 −0.43 −0.39 −0.27 630° C.-2 hrs 725° C.-4 hrs −0.91 −0.33 −0.4 −0.295 −0.19 630° C.-2 hrs 750° C.-4 hrs −1.06 −0.25 −0.9 −0.26 630° C.-2 hrs 775° C.-4 hrs −1.29 −0.74 630° C.-2 hrs 800° C.-4 hrs Example-> 64 65 66 67 68 CIE L* D65 SCE Results As Made Glass Heat Treated Glasses Nucleation Growth Temperature- Temperature- time (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 0.29 0.16 0.19 630° C.-2 hrs 700° C.-4 hrs 0.5 0.19 0.2 0.24 630° C.-2 hrs 725° C.-4 hrs 0.37 0.29 0.45 0.24 0.47 630° C.-2 hrs 750° C.-4 hrs 0.3 0.25 0.31 0.4 0.51 630° C.-2 hrs 775° C.-4 hrs 0.72 0.48 0.43 4.24 3.8 630° C.-2 hrs 800° C.-4 hrs CIE a* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs −0.08 0.08 −0.02 630° C.-2 hrs 700° C.-4 hrs −0.11 0.04 −0.09 0 630° C.-2 hrs 725° C.-4 hrs −0.06 0.01 0.04 −0.02 0.03 630° C.-2 hrs 750° C.-4 hrs −0.05 −0.06 −0.07 0.03 0.07 630° C.-2 hrs 775° C.-4 hrs −0.08 −0.04 −0.01 −0.61 −0.55 630° C.-2 hrs 800° C.-4 hrs CIE b* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs −0.37 −0.41 −0.29 630° C.-2 hrs 700° C.-4 hrs −0.45 −0.4 −0.34 −0.32 630° C.-2 hrs 725° C.-4 hrs −0.61 −0.31 −0.41 −0.45 −0.45 630° C.-2 hrs 750° C.-4 hrs −0.5 −0.35 −0.25 −0.62 −0.88 630° C.-2 hrs 775° C.-4 hrs −1.03 −0.76 −0.74 −4.41 −3.93 630° C.-2 hrs 800° C.-4 hrs Example-> 69 70 71 CIE L* D65 SCE Results As Made Glass Heat Treated Glasses Nucleation Growth Temperature- Temperature- time (T_(n)-t_(n)) time (T_(c)-t_(c)) 630° C.-2 hrs 675° C.-4 hrs 0.28 0.27 0.2 630° C.-2 hrs 700° C.-4 hrs 0.19 0.15 0.21 630° C.-2 hrs 725° C.-4 hrs 0.25 0.22 1.18 630° C.-2 hrs 750° C.-4 hrs 0.39 0.49 2.04 630° C.-2 hrs 775° C.-4 hrs 3.43 4.38 4.72 630° C.-2 hrs 800° C.-4 hrs CIE a* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-tn Tc-tc 630° C.-2 hrs 675° C.-4 hrs 0.03 0.11 0.12 630° C.-2 hrs 700° C.-4 hrs 0.04 0.07 0.09 630° C.-2 hrs 725° C.-4 hrs 0.1 0.09 0 630° C.-2 hrs 750° C.-4 hrs 0.12 0.05 −0.01 630° C.-2 hrs 775° C.-4 hrs −0.43 −0.7 −0.13 630° C.-2 hrs 800° C.-4 hrs CIE b* D65 SCE Results As Made Glass-> Heat Treated Glasses Tn-t_(n) Tc-t_(c) 630° C.-2 hrs 675° C.-4 hrs −0.36 −0.34 −0.22 630° C.-2 hrs 700° C.-4 hrs −0.37 −0.33 −0.34 630° C.-2 hrs 725° C.-4 hrs −0.4 −0.33 −1.66 630° C.-2 hrs 750° C.-4 hrs −0.84 −1.02 −2.67 630° C.-2 hrs 775° C.-4 hrs −3.11 −4.36 −5.29 630° C.-2 hrs 800° C.-4 hrs

TABLE V Heat IOX IOX Time thickness CS DOL Ex treat Temp (hrs.) (mm) (MPa) (um) 53 630-2 430 14 0.75 949.3 50.9 57 630-2 430 14 0.76 957.9 49.8 59 630-2 430 14 0.76 941.3 49.8 — 630-1 430 14 0.77 952.6 48.9 61 630-2 430 14 0.74 915.1 48.5 66 630-2 430 14 0.78 859.8 37.8 68 71 630-2 430 14 0.76 938.3 56.2 53 630-2 410 8 0.75 1012.2 31.8 57 630-2 410 8 0.78 1024.7 28.4 59 — 630-2 410 8 0.79 1046.9 29.7 61 630-2 410 8 0.75 990.1 30.3 66 68 630-1 410 8 0.79 1053.4 30.4 71 630-2 410 8

Tables II-IV show various properties of the crystallizable glasses and glass-ceramics formed from the Example Compositions in Table I. In Table II, reference to “Amorph” refers to amorphous, “Fay” refers to Fayalite, “Hem” refers to Hematite, “PB” refers to pseudobrookite, and “Mag” refers to Magnetite. Also in Table II, reference to α (10⁻⁷/° C.) refers to the coefficient of thermal expansion. Table V includes some heat treatment conditions and IOX conditions, and CS/DOL measurements using FSM, for selected crystallizable glasses, just after nucleation. FSM measurements were used at this stage due to the transparency of the crystallizable glasses. Glass-ceramics exhibit an opacity that does not permit the visible light transmission required for FSM measurements.

The Example Compositions 1-7, 14-17, 43-44, 53, 57, 60, 63 and 71 melted to defect-free fluid homogeneous liquids. All of Example Compositions 1-7, 14-17, 43-44, 53, 57, 60, 63 and 71 formed dark amber colored glasses that were transparent, except for Example Compositions 1 and 5-7 which were black and opaque after annealing. All of the resulting glass-ceramics made from Example Compositions 1-7, 14-17, 43-44, 53, 57, 60, 63 and 71, except for the glass-ceramics made from Example Composition 2, were black and opaque or nearly opaque. The glass-ceramic made from Example Composition 2 exhibited no visual change after ceramming and remained transparent. FIG. 1 compares the transmission spectra for visible and IR wavelengths obtained for as-made and heat treated glasses of Example Composition 15 and indicates the as-made glass transmits sufficiently to enable efficient melting.

The viscosity of selected Example Compositions from Table 1 was measured by beam bending, disk compression, and rotating cylinder methods according to ASTM standards C1350M-96, C1351M-96, and C965-96 respectively to cover the entire range from strain point to 10 Pa*s. The liquidus was measured by 72 hour gradient boat, density by Archimedes, and thermal expansion by dilatometer according to ASTM standards. FIG. 4 shows the viscosity versus temperature curve denoting the liquidus temperature and viscosity for the glass of Example 15.

Glasses made from selected Example Compositions were then cut into pieces for forming glass-ceramics. The glasses were heated at 5° C/min to 630° C. for 2 hours to nucleate the glass, and then heated to the final growth temperature, held for 4 hours, and cooled to room temperature at furnace rate, resulting in glass-ceramics. Since all samples were nucleated at 630° C. for 2 hours, it is to be assumed all glass-ceramics were first nucleated at 630° C. unless otherwise specified; hence the heat treatment nomenclature “750-4” corresponds to a sample nucleated at 630° C. for 2 hours with a final ceram hold at 750° C. for 4 hours and the heat treatment nomenclature “700-4” corresponds to a sample nucleated at 630° C. for 2 hours with a final ceram hold at 700° C. for 4 hours, etc.

Glasses formed from Example Compositions 2-4, 14-17, 43-44, 53, 57, 60, 63 and 71 were amorphous after annealing. Glasses formed from Example Compositions 1 and 5-6 exhibited magnetite peaks and Glass 7 exhibited magnetite and ϵ-Fe₂O₃. FIG. 7 shows exemplary x-ray diffraction patterns for the 4 types of patterns observed: amorphous, ϵ-Fe₂O₃, (JCPDS 00-016-0653), pseudobrookite (JCPDS 00-041-1432), and magnetite (JCPDS 01-076-2948). Curve “a” in FIG. 7 shows the pattern for a glass-ceramic made from Example Composition 3 after being heat treated at 750-4, which exhibits peaks matching magnetite. Small pieces (<1 mm) of this could be picked up by a magnet as could all the compositions which exhibited a magnetite diffraction pattern. Curve “b” in FIG. 7 shows the pattern for a glass-ceramic made from Example Composition 16 after being heat treated at 750-4. Curve “c” in FIG. 7 shows the pattern for a glass-ceramic made from Example Composition 53 after being heat treated at 750-4. Curve “d” in FIG. 7 shows the pattern for a glass made from Example 16 after annealing. The intensity of the magnetite peaks in the glass-ceramics increased from Example Composition 3 to Example Composition 6, as did the size of the glass-ceramic particles that stuck to the magnet. The glasses/glass-ceramics exhibiting pseudobrookite and ϵ-Fe₂O₃ did not stick to a magnet even for pieces <0.1 mm. As shown in FIG. 7, the glass formed from Example Composition 16 was amorphous after annealing but exhibited peaks corresponding to pseudobrookite after ceramming, as shown by curve “b”. Example Composition 53 expressed ϵ-Fe₂O₃ peaks when cerammed at 750° C. as shown by curve c in FIG. 7 and even fainter ϵ-Fe₂O₃ peaks when cerammed at 700° C.

FIG. 2 shows the X-ray diffraction (XRD) pattern obtained for a glass-ceramic made from Example Composition 3, after heat treating at 700° C. for 4 hours, illustrating the presence of Magnetite (Fe₃O₄). FIG. 3 shows the XRD pattern obtained for a glass-ceramic made from Example Composition 16, after heat treating at 750° C. for 4 hours, illustrating the presence of pseudobrookite for which line broadening analysis suggests crystallite sizes of roughly between 15-20 nm.

The dielectric constant and loss tangent of selected glass-ceramics were measured from 400 to 3000 MHz on 12 mm long, 3.5mm diameter rods at Microwave Properties North (325 Wylie Road, Deep River, Ontario, Canada KOJ1P0) using the cavity perturbation technique. Optical spectra were measured on a PerkinElmer Lambda 950 UV-Vis-NIR Spectrophotometer from 2500 to 200 nm with 2 nm data interval using 0.8 mm thick samples. In situ high temperature measurements were made on the same instrument using a joule heated hot stage with 0.5 mm thick 13 mm diameter samples under a nitrogen atmosphere to prevent oxidation of the stainless steel sample holder and maintain good thermal contact with the small sample.

FIG. 8 shows the average dielectric constant and loss tangent as a function of R₂O—Al₂O₃ for glass-ceramics made from Example Compositions 2-6, after ceramming at 750-4, over the frequency range of 400 to 3000 MHz. FIG. 8 also shows the dielectric constant and loss tangent as a function of R₂O—Al₂O₃ for glass-ceramics made from Example Composition 7, after ceramming at 750-4, over the frequency range of 400 to 3000 MHz (shown as individual points in FIG. 8). These data represent a composition set examining alkali to alumina contents at constant Fe₂O₃ level plus Example Composition 7, with 2 mole % TiO₂ at R₂O—Al₂O₃=0. Since the dielectric constant K for each glass-ceramic varied by less than 4% over the frequency range measured, an average was used to represent the featureless spectral data for simplicity. The loss tangent was a linearly increasing function of frequency and increased by 0.005 +/−0.002 from 400 to 3000 MHz. The dielectric constant shows a discontinuity versus excess alkali at the charge balanced composition where R₂O═Al₂O₃, while the loss tangent was a sigmoidally decreasing function of excess alkali (R₂O—Al₂O₃). When 2 mole % SiO₂ from the charge balanced composition of Example Composition 4 was replaced with 2 mole % TiO₂ to make Example Composition 7, the cerammed phase shifted from magnetite to pseudobrookite and the dielectric constant jumped to 7.8 while the loss tangent increased to 0.027.

The black, magnetite-containing glass-ceramics provide the opacity and other desirable, non-magentic properties for electronic device applications. In other applications, such as appliances, the glass-ceramics exhibit magnetic properties that are desirable. The amount of TiO₂ in Example Composition 7 started to shift the crystallite phase away from magnetite as pseudobrookite and ϵ-Fe₂O₃ also precipitated; however, the material spontaneously formed crystals in the annealed precursor glass and its loss tangent was the highest of all the glasses studied thus far. Consequently Example Compositions 14-17 and 43-44 were formulated to explore the newly found pseudobrookite and ϵ-Fe₂O₃ composition space and lower the total Fe₂O₃ content to decrease the loss tangent.

The dielectric constant and loss tangent for glass-ceramics with a lower Fe₂O₃ content (e.g., glass-ceramics formed from Example Compositions 15, 43 and 44, which are plotted in FIG. 9), show the large decrease in dielectric constant and loss tangent with decreasing Fe₂O₃ content. It should be noted that Example Composition 43 also has a lower TiO₂ content and a greater SiO₂ content than Example Compositions 15 and 44, which could also contribute to the more rapidly decreasing loss tangent and dielectric constant between 0.6 and 0.5 mole % Fe₂O₃.

FIG. 10 shows the transmission spectra of crystallizable glasses made from Example Composition 15 as a function of heat treatment. The samples of crystallizable glass were placed on lined paper and had dimensions of 25 mm×25 mm×0.8 mm. The samples were amber, yet transparent, after annealing. After the samples were nucleated at 630° C. and cerammed at 700° C. and 750° C., respectively, for 4 hours, they were pitch black and opaque, even at a thickness of about 0.8 mm. The transmission increases at wavelengths longer than 1500nm, with samples heat-treated at lower temperature exhibiting higher IR transmission.

The kinetics of crystallization were investigated by measuring the transmission of sheets of selected glasses during the ceramming process. An un-annealed sheet of glass was prepared from Example Composition 60 and had a thickness of about 0.5 mm. The glass sheet was heated in a hot cell in a spectrophotometer. FIG. 11 shows the temperature of the sample and the transmission as a function of time during heat up, nucleation, and crystal growth. The transmission at 400 nm diminished rapidly as the sample was heated to the 630° C. nucleation temperature. The transmission across the visible portion of the spectrum then followed suit and slowly declined during the nucleation hold. Then the temperature was raised to 700° C. near 200 min where the remaining transmission plummeted to 0 over the next 60 minutes. The nucleation step is significant and omitting the nucleation step and thus hold at 630° C. results in samples with greater than 75% of the transmission of annealed samples even with 4 hour holds at 700 or 750° C. The extinction spectra of glass-ceramics made from Example Composition 53 after various heat-treatments are plotted in FIG. 12. The UV edge shifts to longer wavelengths and the absorption band at 1100 nm increases up until a ceram temperature of 750° C. At higher ceram temperatures, the 1100 nm absorption band begins to diminish and the UV edge shifts back to shorter wavelength. This trend continues to 850° C. where the glass begins to noticeably soften. The absorption at 650, 700, 1100, 1500, 2000, and 2500 nm are plotted as a function of ceram temperature in the insert in FIG. 12 to illustrate this behavior, clearly showing the peak in opacity at 750° C. An XRD confirmed that the phase remains ϵ-Fe₂O₃ at 800° C. Decreasing opacity with increasing ceram temperatures above 750° C. was also observed visually with intense backlighting of the sample and confirmed spectroscopically in glass-ceramics made from Example Compositions 15 and 43-44, 53, 57, 60, 63 and 71. The color of these samples was blackest for ceram temperatures between 700 to 750° C. and then began to turn noticeably grey with increasing ceram temperatures at or above 775° C. Ceram temperatures below 700° C. resulted in amber samples with visibly noticeable transmission.

The electron energy loss spectra (EELS) of the Fe and Ti in the nanocrystals of selected glass-ceramics made from the Example Compositions of Table 1 were measured to see if the opacity maximum was the result of an oxidation state change. At least 5 nanocrystals from each heat treatment were measured, curve fit to standard Fe²⁺ and Fe³+ spectra and then plotted as a function of ceram temperature in FIG. 13. Glass-ceramics made from Example Compositions 53, 60, and 71 were measured and all showed a minimum in the Fe³⁺/Total Fe ratio at a heat treatment temperature of 775° C., indicating that Fe²⁺ in the nanocrystals is maximized with this heat treatment. Larger nanocrystals in the sample were chosen from the thinnest section of the TEM sample to avoid signal from the glass and obliteration of smaller nanocrystals from beam damage. Thus only a small fraction of nanocrystals were suitable for analysis and each had significantly different compositions, so the ensemble average of analyzed crystals for each ceram temperature is plotted in the FIG. 13 inset. The nanocrystallites in the 675 and 700° C. heat treated samples were too small for analysis.

To obtain the EELS data, electron thin samples (<100 nm) of selected glass-ceramics were prepared with a FEI Quanta focused ion beam (FIB) system using the very gentle sample preparation technique as described below. The main pit was milled at 30 KeV 5 nA (20 um×10 um×2 um). The first facing was done using 30 KeV at 1 nA to a thickness of 1 um. To reduce damage to the sample during the preparation the final polishing was done at 5 KeV at 150 nA to less than 100 nm. To remove the leftover Ga during the FIB-ing process the final cleaning was done at 2 KeV and 0.083nA. It has been hypothesized before that for every KeV increase in the FIB voltage there is ˜1 nm thick damaged layer. Thus using the final 2 KeV for cleaning, the damage layer is only ˜2 nm. To reduce damage during imaging, the TEM was done at 80 KeV at a low extraction. This reduced the electron dose on the sample during imaging. The composition of the particles was calculated. EELS spectra for Fe and Ti were collected using a Gatan Quantum® GIF with high dispersion of 0.05 eV/channel. As the zero loss peak (ZLP) had 0.8 eV resolution, it was possible to capture all the salient features of the Fe and Ti L₂₃ edges.

FIG. 14A shows the TEM micrograph of a glass-ceramic made from Example Composition 60, after being cerammed at 750° C., for 4 hours. The image of FIG. 14A shows the ˜20 nm crystallites, while the elemental maps of FIG. 14B show that the crystallites are enriched in Fe, Ti, and Mg and depleted in Si, Al, and Na. The compositions of at least 5 crystallites from the glass-ceramics made from Example Compositions 53 and 71 were measured and averaged for each heat treatment by EELS and superimposed on the 1000° C. MgO—TiO₂—Fe₂O₃ phase diagram shown in FIG. 15. The Fe₂O₃, MgO, and TiO₂ contents of the Example Compositions 53 and 71, excluding other components, were also plotted for comparison. The crystallites in Example Composition 53 were almost spherical at all temperatures similar to those in FIGS. 14A and 14B, while Example Composition 71 had additional elongated crystallites, so the compositions of both morphologies were measured and plotted separately in FIG. 15. The crystallites formed at 675° C. and 700° C. were too small to analyze by TEM, but the 725° C. samples had ϵ-Fe₂O₃ crystallites on the α′-Fe₂O₃ (hematite) α-MgTiO₃ (geikielite) tie line for both glasses. As the ceram temperature was increased to 750° C., the composition of the crystallites shifted along the tie line towards MgTiO₃. When cerammed at 775° C., the composition of the crystallites in the glass-ceramic made from Example Composition 53 continued to enrich in MgTiO₃ at the expense of Fe₂O₃, while the crystallites of both morphologies in the glass-ceramic made from Example Composition 71 began to shift to the TiO₂ rich side of the tie line at 775° C. At the 800° C. ceram temperature the elongated crystallites in Example Composition Glass 71 were on the pseudobrookite tie line, the spherical crystals on the α′-Fe₂O₃ (hematite) α-MgTiO₃ (geikielite) tie line, and the samples expressed both pseudobrookite and ϵ-Fe₂O₃ in XRD. X-ray diffraction data suggests these correspond to the elongated and spherical crystallites respectively. The crystallites in both compositions became richer in Fe₂O₃ as the ceram temperature was increased from 775 to 800° C. The compositions of the elongated crystallites in the glass-ceramics made from Example Compositions 53 and 71, after being cerammed at 850° C. were both on the pseudobrookite tie line with those of Example Composition 53 (i.e., close to pure Fe₂TiO₅).

Glass-ceramics samples were formed from Example Compositions 53 and 71. The crystallizable glasses were formed and nucleated at 630° C. for 2 hours and then cerammed for 4 hours each at the temperatures shown below in Table VI. Table VI also shows the elemental compositions of the crystallites present in the resulting glass-ceramics formed from Example Compositions 53 and 71.

TABLE VI Elemental composition of crystallites. Morphology Ceramming Spherical Crystals Elongated Crystals Temperature (mol %) (mol %) (° C.) Fe₂O₃ MgO TiO₂ Fe₂O₃ MgO TiO₂ Example Composition 53 725 39.7 29.8 30.5 44.1 23.4 32.5 750 23.4 39.3 37.3 21.1 43.1 35.9 775 22.8 36.7 40.5 18.9 40.1 41.0 800 55.5 16.1 28.4 61.0 14.1 24.9 Example Composition 71 725 24.7 31.6 43.7 24.3 32.7 42.9 750 17.3 31.3 51.4 11.1 42.5 46.4 775 18.8 28.6 52.6 10.6 37.0 52.4 800 27.8 29.6 42.5 21.2 19.1 59.6

Glass-ceramic samples were formed from Example Compositions 57, 70, 71, 114 and 53. The Example Compositions were nucleated for 2 hours at 630° C. and cerammed at the temperatures shown in FIG. 16. The resulting glass-ceramics had a thickness of about 0.8 mm. It was observed that glass-ceramics formed from these Example Compositions having about 1-2 wt % Fe₂O₃, about 1-2 wt % TiO₂, about 0-0.5 wt % MnO₂ and 0-0.5 wt % SnO₂ all exhibited a dark black color. Increasing the ceramming temperature, however, changed the opaque glass-ceramics from exhibiting a black color to a gray color, which can increase the transmission. It was observed that at peak ceramming temperatures of about 775° C. or greater, the color of the glass-ceramics turned from black to gray. FIG. 16 shows a drastic increase in transmission through the samples as the ceramming temperature was increased above 725° C. The glass-ceramics exhibiting a greater L* value exhibited higher transmission and, in some cases, exhibited an amber color.

To understand the causes of the changes in optical properties (e.g., L), Example Compositions 52, 60 and 71 were evaluated in greater detail with respect to the change in Fe/Ti ratio. As shown in Table VII, Example Composition 60 had the highest Fe content (an greatest Fe/Ti ratio) and Example Composition 71 had the lowest Fe content (and lowest Fe/Ti ratio).

TABLE VII Fe/Ti and Fe/Mg ratio of Example Compositions 53, 60 and 71. Example Composition 71 53 60 Fe/Ti 1.02 1.16 1.43 Fe/Mg 1.65 1.28 1.6

Glass-ceramics were formed from Example Compositions 53, 60 and 71 by nucleating the crystallizable glasses at 630° C. and ceramming at 800° C. for 4 hours or 775° C. for 4 hours. FIGS. 17-19 show the XRD traces of the glass-ceramics formed from Examples 53, 60 and 71. As shown in FIG. 17, the glass-ceramics formed from Example Composition 71 show predominantly pseudobrookite and little ϵ-Fe₂O₃. As shown in FIGS. 18-19, the glass-ceramics formed from Example Composition 53 and 60 (which were cerammed at a lower temperature of about 775° C.) exhibited predominantly ϵ-Fe₂O₃ crystals. The data from FIGS. 17-19 indicates that above a certain Fe/Ti ratio, the final crystallites in the glass-ceramics include ϵ-Fe₂O₃. Where the content of Ti is higher, crystallites include pseudobrookite. This is represented in the phase diagram (Fe₂O₃—FeO—TiO₂) shown in FIG. 20. Pseudobrookite is a solid solution of Fe^(III) ₂TiO₅ and Fe^(II)Ti₂O₅ and is black in color, but not magnetic.

FIG. 21 shows high angle annular dark field (“HAADF”) or Z-contrast images of a glass-ceramic formed from Example Composition 53, after nucleating at 630° C. for 2 hours and ceramming at 800° C. for 4 hours. The corresponding Energy Dispersive X-Ray Spectroscopy (EDS) maps of Fe, Ti and Mg elements are also shown in FIG. 21. The brighter or lighter colored areas indicate crystalline areas. The length scale at the bottom of each EDS map indicates 200 nm. The EDS maps show the presence of Mg in all the particles of the glass-ceramic. In the Example Compositions shown in FIG. 21, Mg was detected in the crystals for all the compositions, cerammed at different temperatures.

Various glass-ceramics were made from Example Compositions 53 and 71 and cerammed at different temperatures. FIGS. 22A and 22B shows the graphical representation of the quantitative data with ceramming temperature. The data indicates that for glass-ceramics made from Example Compositions 53 (and which include both spherical and elongated morphological particles), the Fe content in the crystallites decreases as the ceramming temperature increases from 725° C. to 750° C. and the amount of Mg and Ti increases. When the ceramming temperature is 750° C., the mol % of both Fe and Mg in the crystallites varied between 25 mol % to 35 mol %. When the ceramming temperature exceeded 750° C., Mg and Ti in starts to leave the crystallites and the crystallites become rich in Fe. This conclusion corresponds well with the transmission data of FIG. 16, which shows a minima at the ceramming temperature of 750° C. The data for glass-ceramics formed from Example Composition 71, which includes a higher TiO₂ content relative to Example Compositions 53 and 60, differs. The composition of the elongated crystallites in the glass-ceramics formed from Example Composition 71 shows a steady increase in Ti as ceramming temperature increases, but the amount of Fe and Mg in the crystallites follows the same trend as the glass-ceramics from Example Composition 53. On the other hand, the spherical crystallites follow the same trend as the glass-ceramics formed from Example Composition 53, but the composition of the individual elements (Fe, Ti and Mg mol/%) is different. In the glass-ceramics formed from Example Composition 71, both the spherical and elongated crystallites include Fe and Mg in the range from about 25 mol % to 35 mol % at 725° C. The spherical particles (which include the majority of the crystallites) maintains this composition even when the ceramming temperature is increased to 775° C.; however, the elongated particles (which include the minority of the crystallites) have an increased amount of Ti (in mol %). Transmission data from FIG. 16 supports this because transmission remains almost constant up a ceramming temperature of 750° C., after which transmission starts increasing. Thus, without being bound by theory, it appears that to achieve the lowest transmission, the Fe and Mg content in the majority of the crystallites should be maintained in the range from about 25 mol % to about 35 mol %. These values of the particles are plotted on the MgO—Fe₂O₃—TiO₂ phase diagram (in wt %) as shown in FIG. 15. The crystals from the glass-ceramics made from Example Composition 53 lay right on top of the Fe₂O₃—MgTiO₃ (ϵ-Fe₂O₃) tie line. The crystallites in the glass-ceramics made from Example Composition 71 are enriched in TiO₂ relative to the tie line. Glass-ceramics made from either composition and cerammed at the highest ceramming temperature (i.e., 800° C.) exhibited the highest Fe content crystallites and the glass-ceramics that exhibited the next highest Fe content crystallites were cerammed at the coolest ceramming temperature (i.e., 725° C.). The glass-ceramics that were cerammed at intermediate ceramming temperatures (e.g., 725° C. and 750° C.) exhibited the darkest color and the lowest amount of Fe. Thus the dark glass-ceramic formed from Example Composition 53 (nucleated at 630° C. for 2 hours and cerammed at 750° C. for 4 hours) have crystallites with about the same composition as the crystallites of fading glass-ceramics formed from Example Composition 71 (nucleated at 630° C. for 2 hours and cerammed at 800° C. for 4 hours).

FIG. 23 shows the Fe L₂₃ ELNES for crystallites from glass-ceramics made from Example Composition 53, with increasing ceramming temperatures. The Fe³⁺ main edge is at 709.1 (±0.1) eV with a small shoulder at 707.7 eV. On the other hand the Fe²⁺ edge is at a707.3 (±0.1)eV. The ELNES shows that the crystallites after ceramming at 725° C. are predominantly Fe³⁺, but the amount of Fe²⁺ in the particles increases with increasing ceramming temperature up to 775° C. The amount of Fe²⁺ is then reduced and the crystallites go back to being predominantly Fe³⁺, after this temperature. This change in Fe³⁺ and Fe²⁺ with ceramming temperature is supported by the compositional analysis in which the amount of Mg²⁺ ions in the crystallites increases at ceramming temperatures greater than 725° C., to charge balance some of the Fe³⁺ changes to Fe²⁺. At ceramming temperatures above 775, the amount of Mg²⁺ ions decreases and the Fe returns to its original oxidation state. This indicates that the presence of Fe³⁺ and Fe²⁺ within a crystal provides the desirable black color in glass-ceramics. The oxidation state of Fe is considered significant because, the presence of Fe²⁺ ions are next to Ti ions provides a black color, whereas, the presence of Fe³⁺ ions provides a blue or green color. The interaction of Fe²⁺ and Fe³⁺ ions may also provide some additional color, thus enhancing absorption.

The change in color in the glass-ceramics described herein at higher ceramming temperature could be due to mixture of two different phenomenon: effects due to composition and effects due to scattering. Scattering in these glass-ceramics is due to either an increase in particle size or an increase in the amount (area fraction) of the crystallites in the glass matrix. Without being bound by theory, it is believed that increased scattering is related to the gray coloration observed after ceramming at higher temperatures. FIG. 24 shows representative HAADF STEM images of glass-ceramics made from Example Composition 53, after being cerammed at 725° C., 750° C., 775° C. and 800° C. Qualitatively, the images of FIG. 24 show a progressive increase in the amount of crystallites as the ceramming temperature increases.

HAADF STEM images of glass-ceramics made from Example Composition 73 were also taken at different ceramming temperatures. Image analysis was performed on 4-5 of the images at each temperature to calculate the area fraction and percentage of different particle morphology within the glass matrix of the glass-ceramic. The averages of these values are shown in FIGS. 25A, 25B and 25C. Image analysis shows that in glass-ceramics made from Example Compositions 53 and 71, the area fraction of particles is below about 10% at ceramming temperatures up to about 775° C. As such, it is believed that to minimize the effect of scattering and to achieve a black color, the area fraction of the crystallites in a glass-ceramic may be below about 10%.

Image analysis also indicated that in glass-ceramics made from Example Composition 71, there is a significant increase in spherical particles and a reduction in elongated particles, which are also Ti-rich. This difference suggests that the color exhibited by these glass-ceramics is due to the presence of spherical particles and not the Ti-rich elongated particles.

Other analysis included the CIELAB color space coordinates determination and phase identification by x-ray diffraction.

Among the further processing was an ion exchange treatment of the glass-ceramics. Each glass-ceramic sample was cut into shapes suitable for ion exchange evaluation. The samples are then cleaned to eliminate any residual organic contamination. Each cleaned sample is suspended in a bath of molten KNO₃ and held at between 370° C. and 450° C. After an appropriate number of hours in the bath (e.g., up to about 8 hr or more), the sample is removed, allowed to cool, and washed in deionized water to remove any residual salt. Glass-ceramics according to Example Composition 1-7, 14-17, 43-44, 53, 57, 60, 63 and 71 were immersed in a molten bath of potassium nitrate (with 0.5 wt % silicic acid to prevent etching) having a temperature of about 420° C. or 430° C. between 6.5 and 8 hours in 304 stainless steel containers and baskets. The glass-ceramic samples were then cooled to room temperature, and then washed in deionized water to remove the adhered salt. Following such treatment, the compressive stress and depth of layer were measured using polarized light on an Orihara surface stress meter model FSM-6000 for glasses and an instrument operating at 1550 nm in the NIR to measure the glass-ceramics, which were opaque in the visible spectrum. Stress optical coefficient and refractive index were measured by diametrical compression and critical angle methods respectively to convert FSM birefringence into stress and depth of layer. FIG. 6, shows DOL as a function of CS for selected glass-ceramics. FIG. 6 also shows the possible CS/DOL combinations that were achievable in the glass-ceramics described herein, using different ion exchange patterns. For example, it is possible to provide glass-ceramics having a CS 900-1100 MPa and DOL of between 25-55 microns.

The mechanical performance of the black glass-ceramics obtained from Example Compositions 53 and 60 were measured by three methods: flexural response by ring on ring (ROR) and abraded ring on ring (aROR), and 4 point bend. The ring on ring test evaluates the biaxial flexure strength of the substrate faces, while the 4 point bend test evaluates the strength and finish quality of the edges. Abraded ring-on-ring was used to quantify retained mechanical performance, after having imposed a given flaw population.

Ring on ring strength (biaxial flexure) was measured on 50 mm square samples having a thickness of about 0.8 mm using a 25.4 mm support ring and 12.7 mm load ring and crosshead speed of 1.2 mm/min according to ASTM C1499. To rank the relative strength of the materials after use, samples were abraded with SiC grit according to ASTM C158.

The strength attributes of a commercially available aluminosilicate glass substrate (shown as “Substrate X” in Table VIII and FIGS. 26-28) and the glass-ceramics formed from Example Compositions Glasses 53 and 60, after being heat treated at 700-4 were compared. Both the Substrate X and the glass-ceramic samples were ion-exchanged to the same depth of layer. The glass-ceramics were ion exchanged at a higher temperature than the Substrate X samples as shown in Table VIII, to better match the compressive stress of the Substrate X samples.

TABLE VIII Heat treatment and ion exchange conditions and resulting strength properties. Glass- Glass- ceramic ceramic formed formed from from Ex. Ex. Substrate Comp. Comp. Sample X 53 60 Heat Nucleation (° C.-hr) None 630-2 630-2 Treatment Growth (° C.-hr) None 700-4 700-4 IX Temperature (° C.) 420 430 430 Time (hr) 6.5 8 8 CS (MPa) 848 998 1060 DOL (μm) 43 41 41 Strength ROR (N) 2350 2852 2974 aROR (N) 961 1284 1321 4 pt Bend (MPa) 709 838 848

FIG. 26 shows the ring on ring load to failure distribution of 30 samples of the glass-ceramics and Substrate X, both before and after ion exchange (all samples had a thickness of about 0.8 mm). Load to failure is reported because the strength of the ion exchanged samples was so high that bending displacement was large enough to make the membrane stresses non-negligible. Therefore, conventional failure stress calculations would overestimate the material stress at failure. While strain gauges would enable calculation of the true stress, they increase the stiffness of the sample and alter the very surface under test and create an additional source of error. Thus, rather than report an inflated strength value (stress at failure) Table VIII and FIG. 26 shows the load to failure which is directly measured without any assumptions or estimations for an unbiased ranking of relative strength for the biaxial flexure tests. The Weibull modulus and characteristic life, which is the 63.2 percentile (1-1/e) of the data, are reported in FIGS. 26-28 for comparison. Before ion exchange, comparative Substrate X had a characteristic life load of 381 N, while the glass-ceramics made from Example Compositions 53 and 60 exhibited similar characteristic life loads of 437 and 459 N, respectively. After ion exchange, the lifetime load to failure for Substrate X increased to 2371 N, the glass-ceramic formed form Example Composition 53 increased to 2825 N and the glass-ceramic formed from Example Composition 60 increased to 2965 N. The 95% confidence intervals (dashed lines) of both glass-ceramics in FIG. 16 were overlapping indicating no significant difference between them, but both were significantly higher than Substrate X. The slopes of the failure probability lines significantly steepened with ion exchange, increasing the Weibull modulus from between 2.9 and 4.6 for the non-ion exchanged glass-ceramic and Substrate X samples up to between 15 and 19 for the ion exchanged glass-ceramic and Substrate X samples.

To determine the biaxial performance after in-use conditions, the parts were abraded with 1 ml of SiC particles at 34kPa pressure and then tested using the same ring-on-ring test configuration as used in FIG. 26. Abrasion in this way imposes flaws of roughly 20 μm in depth and serves as a surrogate for what the material being tested would encounter in the field. FIG. 27 shows that Substrate X samples, glass-ceramic samples made from Example Composition 53, and glass-ceramic samples made from Example Composition 60 had 961 N, 1283 N, and 1321 N characteristic life loads, respectively. Once again, the two glass-ceramics were indistinguishable, and significantly better than the glass. All had similar Weibull moduli between 6 and 9. The four point bend data shown in FIG. 28 shows that the non-ion exchanged samples all had characteristic strengths between 120 and 140 MPa. After ion exchange, the Substrate X samples strength increased to 709 MPa, while the strength of the glass-ceramic samples made from Glasses 53 and 60 increased to 838 and 848 MPa, respectively, all with Weibull moduli between 35 and 60. Both glass-ceramics were significantly stronger than Substrate X, but indistinguishable from each other.

While crystallizable glasses formed from Example Composition 1 exhibited a liquidus viscosity of about 1.2 kPa*s, crystallizable glasses formed from Example Compositions 53 and 71 exhibited liquidus viscosities that exceeded 100 kPa*s. All of the glasses measured had strain points near 560° C., anneal points close to 615° C., and softening points near 895° C. The spontaneous magnetite precipitation in the crystallizable glass made from Example Composition 1 indicates that 2.16 moles of Fe₂O₃ exceeds the solubility limit for this composition. This is also manifested as a high liquidus temperature of 1235° C. with magnetite as the liquidus phase. Example Composition 1 may be useful for a spontaneous black magnetic glass-ceramic, it would not be suitable for making precision glass sheets, due to its low liquidus viscosity of 1.2 kPa*s.

Example Compositions 2-6 showed the large impact of excess alkali (R₂O—Al₂O₃) on Fe₂O₃ solubility. Example Composition 2 with 2 moles of excess alkali is grossly under-saturated in Fe₂O₃ and remained amorphous even after ceramming. Decreasing the excess alkali to 1 mole % results in a stable glass, that cerams to a black magnetite glass-ceramic, with just over 40 kPa*s liquidus viscosity—more than adequate for any forming operation. Once the alumina content exceeds the alkali, spontaneous magnetite precipitation is now even observed at 1.8 mole % Fe₂O₃ demonstrated by Example Compositions 5 and 6.

The excess alkali also affected the dielectric properties of the glass-ceramics. The lower solubility of magnetite on the alumina rich side of FIG. 8 resulted in more magnetite precipitating and correspondingly, a higher loss tangent. This was verified with XRD that showed the glass-ceramics exhibited increased integrated magnetite peak intensity at negative R₂O—Al₂O₃ that decreased to 0 as the excess alkali was increased to 2. Magnetite nanocrystals are reported to have a high dielectric loss tangent around 1.2 at about 3 GHz and magnetic losses around 0.5 depending of the size and structure of the magnetite particles. Thus the magnetite loss in known materials is 50 times greater than glass-ceramics made from Example Compositions 2-6, which could contain at most 1.2 mole % Fe₃O₄ implying the minority magnetite phase in these glass-ceramics contributes 1.2 loss tangent*1.2%=0.014 to the loss tangent or the majority of the 0.025 loss tangent of glass-ceramics made from Example Composition 6. However, the Fe₂O₃ free glass of FIGS. 26-28 has a dielectric constant of 7.17 and an average loss tangent of 0.022, which is only 0.003 less than the glass-ceramic made from Example Composition 6 (which includes magnetite). It has also been demonstrated that the loss tangent of magnetite could be reduced by more than an order of magnitude by keeping the fine magnetite dispersed and free of large particles. This explains why the magnetite-containing glass-ceramics have a lower than expected loss tangent that is only 0.003 higher than the iron free glass.

Since magnetite raises the dielectric loss tangent and causes magnetic interference, TiO₂ was added to Example Compositions 7, 14-17, 43-44, 53, 57, 60, 63 and 71, to avoid the formation of magnetite and other magnetic phases. The presence of TiO₂ shifted the phase out of magnetite and into ϵ-Fe₂O₃ at TiO₂/Fe₂O₃ ratios between 1 and 2, and into pseudobrookite (Fe₂TiO₅—MgTi₂O₅ ss) as the TiO₂/Fe₂O₃ ratio approached or exceeded 2 in Table I. The formation of the ϵ-Fe₂O₃ phase is surprising since ϵ-Fe₂O₃ is very hard to make, requiring oxidation of atomized iron in an electric discharge or the transformation of nanoparticles of γ-Fe₂O₃ (maghemite) well dispersed in a silica gel, none of which even yield phase pure ϵ-Fe₂O₃. In one or more embodiments, the formation ϵ-Fe₂O₃ is enhanced by keep the particles well dispersed. If the particles are allowed to agglomerate, they convert to maghemite at elevated temperatures. ϵ-Fe₂O₃ is a non-collinear ferrimagnet with a Curie temperature near 200° C. and has a very large coercivity of 20 kOe and saturation magnetization of 25 emu/g; however the ϵ-Fe₂O₃ glass ceramics of the embodiments described herein did not stick to a magnet like the magnetite glass-ceramics.

The lack of obvious magnetism may be explained by the understanding that small ϵ-Fe₂O₃ particles synthesized at 700° C. were superparamagnetic exhibiting zero remnant magnetization and zero coercivity. It is also understood that ϵ-Fe₂O₃ particles must reach a threshold size before its magnetocrystalline anisotropies could cause high coercivities and that low magnetization is achieved with small ϵ-Fe₂O₃ particles as the TEM images depict. Furthermore, FIGS. 14A, 14B and 15 demonstrated that the nanocrystallites in the glass-ceramics with the ϵ-Fe₂O₃ structure are not pure Fe₂O₃, but a solid solution of MgO, TiO₂, and Fe₂O₃, which could disrupt the magnetic ordering of ϵ-Fe₂O₃ made up of Fe₂O₃ alone. The glass-ceramics described herein also have a large fraction of Fe²⁺, unlike the pure Fe₂O₃ based ϵ-Fe₂O₃ which is nominally all Fe³⁺. Finally, all of the glass-ceramic compositions that expressed ϵ-Fe₂O₃ had 2.4 times less total Fe₂O₃ than those expressing magnetite, so the total number of unpaired spins is lower in the ϵ-Fe₂O₃ glass-ceramics reducing the magnetization by more than half. Thus, the small size, compositional complexity, mixed valence state, and lower total Fe content all can contribute to the fortuitously low magnetization of the ϵ-Fe₂O₃ glass-ceramics.

It was also noticed that the compositions of the ϵ-Fe₂O₃ nanocrystals plot right across the gap in the rhombohedral phase field (α′-Fe₂O₃ (hematite) α-MgTiO₃ (geikielite) tie line) in FIG. 15. It has been reported that the gap gets smaller with decreasing temperature, but this has not been investigated below 1000° C. due to slow equilibration kinetics. However it is understood that the gap in the α′-Fe₂O₃ (hematite) α-MgTiO₃ (geikielite) tie line should disappear in the vicinity of 700° C., which is the temperature regime where the glass-ceramics described herein form ϵ-Fe₂O₃. The ϵ-Fe₂O₃ in glass-ceramics made from Example Compositions 53 and 60 both convert to pseudobrookite when cerammed at 850° C. It should also be pointed out that the pseudo ternary diagram in FIG. 15 is an oversimplification of the crystallite compositions in this glass-ceramic because both Fe²⁺ and Fe³⁺ are simultaneously present (bulk precursor glasses have about 2/3 Fe³⁺ and 1/3 Fe²⁺). The FeO—TiO₂—Fe₂O₃ ternary in FIG. 29 has the same phase relationships as the MgO—TiO₂—Fe₂O₃ diagram in FIG. 15, except that MgO is replaced by FeO and the rhombohedral phase extends all the way from α′-Fe₂O₃ to α′-FeTiO₃, unlike the Fe₂O₃—MgTiO₃ solid solution which exhibits a gap in the middle that decreases with temperature. The MgFe₂O₄ spinel has the same structure and similar XRD pattern to Fe₃O₄ (FeFe₂O₄) magnetite so it is very likely the magnetite phase detected by XRD is actually a solid solution of both spinels, MgFe₂O₄ and Fe₃O₄. FIG. 29 shows that the gap disappears when MgO is replaced with FeO, and the ϵ-Fe₂O₃ crystallites have a mixture of both MgO and FeO. Finally, ϵ-Fe₂O₃ is orthorhombic with a different crystal structure than the rhombohedral isomorphs of α′-Fe₂O₃, α′-FeTiO₃, and α-MgTiO₃. While ϵ-Fe₂O₃ may be metastable, metastable phases can often be formed from the crystallization of glass because metastable phases often require less structural rearrangement from the glass than the stable phase would require. Thus the combination of well dispersed crystals, compositional complexity, low ceram temperature, different structure, and precipitation from a glass all can contribute to the stability of the ϵ-Fe₂O₃ phase and its extensive solid solution.

While TiO₂ additions enabled the formation of non-magnetic black glass ceramics, they also increased the dielectric constant and loss tangent of the glass-ceramic. By lowering the amount of ϵ-Fe₂O₃ and or pseudobrookite to the minimum amount needed to achieve the desired color, the dielectric constant and loss tangent can both be lowered back to below 7.1 and 0.023 respectively as demonstrated by the glasses made from Example Compositions 15, 43and 44 plotted in FIG. 9, which is comparable to the Example Compositions of FIGS. 26-28 with 7.17 dielectric constant, and 0.022 average loss tangent. As a benefit, the lower the amount of the low solubility phase, the lower the liquidus temperature, and correspondingly the liquidus viscosity will be greater.

By taking the low loss of Example Composition 43 and then fine tuning the composition while keeping the minimal amounts of Fe₂O₃ and TiO₂ necessary to achieve opacity and color, the high liquidus viscosity glass-ceramic made from Example Composition 53 was achieved with 135.8 kPa*s liquidus viscosity. An even darker glass-ceramic was achieved by increasing the Fe₂O₃ in the composition by only 0.15% resulting in Example Composition 60, which forms a clear glass, but was completely opaque after ceramming, even with a thickness of about 0.8 mm, yet still had well over 60 kPa*s liquidus viscosity. A benefit of having a clear or transparent glass is that it permits for automated real time automated inspection of defects and assessment of quality before the material is cerammed. A transparent precursor glass is thus recognized as a benefit in manufacturing, since a spontaneous black material would mask the quantity and identity of melting defects such as cord, seeds, knots, and stones that operators need to adjust melting conditions. These defects must be detected swiftly and the melting process tuned to eliminate them, since they can degrade the strength and performance of the material.

To fine tune the color and optimize the heat treatment time of glass-ceramics made from Example Composition 60, the transmission was studied using in-situ transmission measurements during a ceram cycle. The transmission decrease during the 630° C. nucleation hold in FIG. 11 indicates substantial changes occurring in the glass, even though neither TEM nor XRD could detect any signs of crystallization for samples heat treated at 630° C. Without being bound by theory, it is believed that this must be when the nuclei form and that they are too small for either technique (i.e., TEM and/or XRD) to detect without damaging the glass. Difficulty in observing the nucleating phase is not unusual even in ‘traditional’ high crystallinity glass-ceramics but in the case reported here, these materials have less than 2 mole % of the composition available to partition into the crystal. If only a small fraction of that 2 mol % is converting to nuclei, it can be extremely hard to detect. Since the precursor glass is designed to respond thermally and ceram, it is very beam sensitive in the TEM and crystallites below 5 nm cannot be imaged without damaging the glass, nor can meaningful EELS spectra be acquired on features smaller than 15 nm. The precipitous drop in transmission at 700° C. corresponds to the growth temperature of the crystallites.

The maximum in blackness and opacity at a ceramming temperature of about 750° C. followed by diminished opacity and greying at higher temperatures was initially believed that the nanocrystallites were dissolving back into the glass at higher temperatures, but the TEM images showed even larger crystallites with higher ceram temperatures. The areal density of the nanocrystallites was calculated from the TEM images and plotted in FIG. 30 showing an increase in crystallinity with increased ceram temperature, which rules out decreased crystallinity, as the cause of diminished opacity and greying.

The shape of the absorption curves in FIG. 12 coupled with the Fe EELS spectra in FIG. 13 provides insight in understanding the transmission increase with ceram temperatures above 750° C. While the shape of the absorption tail between 400 and 700 nm may resemble scattering, it follows neither a λ⁻⁴ dependence indicative of Rayleigh scattering, nor a λ⁻² dependence indicative of larger particle Mie scattering. It is actually well fit by a λ⁻³ dependence and is most likely the tail of the strong absorption in the visible that makes the material black. If scattering were dominating extinction in the visible, the material would look hazy or white. Accordingly, intense absorption is necessary to make a material black.

The Fe²⁺—Ti⁴⁺ charge transfer band has a very large absorption cross section and results in intense absorption in the visible portion of the spectrum. Even a few tens of ppm of Fe²⁺ and Ti⁴⁺ result in a yellow tint that is detectable by eye. For charge transfer mechanisms to be active, the Fe²⁺ and Ti⁴⁺ must be in close proximity such as next nearest neighbors bound to a common O²⁻ ion. Even though both Fe²⁺ and Ti⁴⁺ are present in the precursor glass, they are at low concentrations, and thus fairly well dispersed resulting only in a dark amber colored glass due to the few Fe²⁺ and Ti⁴⁺ ions in close proximity. However when they are partitioned into the crystallites, they become next nearest neighbors creating an intense absorption band covering most of the visible spectrum. Close inspection of FIG. 12 shows the Fe²⁺ band at 1100 nm reaching a maximum at the 750° C. ceram temperature and then diminishing at higher ceram temperatures in agreement with the 750° C. opacity maximum. The intensity of the charge transfer band must be 0 in the absence of Fe²⁺ and then increases as the Fe²⁺ increases with optimized ceram temperatures.

The EELS spectra of the nanocrystallites provide their composition as well as the Fe²⁺ fraction. The highest fraction of Fe²⁺ occurs at the minimum in Fe³⁺/Total Fe ratio in FIG. 13 at the 775° C. ceram temperature, which is 25° C. hotter than the observed opacity maximum and Fe²⁺ peak in the optical data. FIG. 31 shows the total Fe²⁺ concentration from EELS (Fe²⁺ fraction*Total Fe₂O₃) as well as the MgO content of the crystallites. While the Fe²⁺ peaks at a ceram temperature of 775° C., the MgO peaks at a ceram temperature of 750° C. in agreement with the observed opacity maximum. Fe²⁺—Fe³⁺ and Fe²⁺—Ti⁴⁺ coordination clusters may coexist in the same structure and give rise to both homonuclear Fe²⁺—Fe³⁺ as well as heteronuclear Fe²⁺—Ti⁴⁺ charge transfer bands. The optical absorption data indicates the largest Fe²⁺ concentration occurs at the 750° C. ceram temperature, so there should be an accompanying maximum in both Fe²⁺—Fe³⁺and Fe²⁺—Ti⁴⁺ coordination clusters and charge transfer absorption, since both clusters require Fe²⁺. In addition, it is understood that the local charge misbalance that occurs with the isomorphous substitution of ions facilitates homonuclear charge transfer bands, such as the replacement of Fe²⁺ and Mg²⁺ by Al³⁺ and Fe³⁺ in ferromagnesian silicates. In the case of ϵ-Fe₂O₃, all of the cations are nominally Fe³⁺, so for the structure to accommodate Mg²⁺ and Fe²⁺, Ti⁴⁺ ions or oxygen vacancies must compensate the charge deficit. Either will result in local charge imbalance to lift the degeneracy of the Fe sites giving rise to homonuclear Fe²⁺→Fe³⁺. Thus the higher levels of Mg²⁺ and Fe²⁺ in the ϵ-Fe₂O₃ crystallites are correlated with the opacity of the glass-ceramics and likely explain the absorption maximum at the 750° C. ceram temperature via the greater total absorption intensity of the Fe²⁺—Fe³⁺ and Fe²⁺—Ti⁴⁺ charge transfer bands. At the higher ceram temperatures where the crystallites are larger and the Fe²⁺—Ti⁴⁺ charge transfer band diminished, scattering becomes significant. Pure scattering makes a white material, but when mixed with black, results in the greys observed in the samples cerammed at 800 and 850° C.

The ring-on-ring data provided herein demonstrate that the glass-ceramic mechanical performance and surface finish were no different from that of known glass substrates before ion exchange. After ion exchange, the failure load for the glass and glass-ceramics was increased by a factor of about 6 because the compressive stress induced by the ion exchange process put approximately 1 GPa of compression onto any existing flaws near the surface of the glass or glass-ceramic. This chemically induced compression then needs to be overcome before the flaws can experience tension and subsequent failure. Abraded ring-on-ring data provided an indication of how the material will perform in the field after use, once damage and flaws have been introduced. The black glass-ceramics showed slightly better performance in both the abraded and non-abraded tests. To understand why, the ring-on-ring and 4 point bend results were plotted as a function of ion exchanged compressive stress in FIG. 32 which shows the correlation between compressive stress and load to failure. It should be noted that the 4 point bend measured modulus of rupture, and not edge strength. For samples with the same nominal exchange depths, the higher compressive stress puts a greater compressive force on existing flaws as well as a greater compressive stress below the surface at the depth the damage was driven by abrasion, which is typically on the order of 10 microns deep and well within the 41 micron compressive layer.

It was observed that the compressive stress was higher for the glass-ceramics than the glass Substrate X samples, even though the glass ceramics were ion exchanged for longer time at a hotter temperature, both of which typically reduce the compressive stress for an ion exchanged glass. One reason for this may be that the glass Substrate X samples were quenched into air after fusion draw, while the glass-ceramics were also initially quenched, but they were subsequently cerammed and cooled much slower in an oven at furnace rate resulting in a denser residual glass in the glass-ceramic. It has been demonstrated that annealed glasses have higher compressive stress and lower diffusivities than quenched glasses. Without being bound by theory, this may be why the slowly cooled glass-ceramics have higher compressive stress and strength than their glass counterpart. Without being bound by theory, this may also be the reason why the glass-ceramics needed to be ion exchanged 10° C. hotter and 1.5 hours longer to achieve the same DOL as the Substrate X samples.

The foregoing embodiments describe crystallizable glasses that provide low crystallinity glass-ceramics with high liquidus viscosity. Magnetite, pseudobrookite, and ϵ-Fe₂O₃ glass-ceramics were made by heat treating silicate glasses doped with Fe₂O₃, MgO, and or TiO₂. Extensive solid solution of ϵ-Fe₂O₃ with MgTiO₃ was discovered for ceram temperatures between 675 and 800° C. EELS and optical absorption data showed that the Fe²⁺ content of the crystallites reached a maximum near 750° C. resulting in maximum blackness and opacity because of optimized Fe²⁺—Ti⁴⁺ charge transfer. By keeping the amount of crystalline material minimal, the dielectric losses and liquidus temperatures were minimized providing a first fusion formable oxide glass-ceramic. Utilizing crystallizable glass compositions with fast ion exchange properties and high compressive stress, resulted in glass-ceramics with strengths of 840 to 850 MPa after ion exchange.

Example Compositions 116-170: The Example Compositions listed in Table IX were used to form crystallizable glasses by introducing appropriately batched raw materials to a platinum crucible. The crucible was then placed in a furnace having a temperature up to about 1700° C. The materials were then refined and the molten glasses were then either poured onto a steel plate to make patties of glass, or they were formed into sheet by rolling or down draw.

In particular, crystallizable glasses formed from Example Compositions 116-170 were melted by mixing 2500 g of batched raw materials in a 1.81 platinum crucible, which was then placed in a SiC globar furnace having a temperature of about 1600° C. for 5 hours. The melted materials were then poured a thin stream into a bucket of flowing cold water to make cullet. The cullet was then remelted at 1650° C. for 5 hours to obtain a homogeneous melt and then poured onto a steel table and subsequently annealed for 2 hours at about 620° C.

TABLE IX Ex. SiO₂ Al₂O₃ B₂O₃ Li₂O Na₂O K₂O MgO CaO SnO₂ 116 64.277 13.240 5.369 0    13.794 0.002 2.040 0.036 0.003 117 64.306 13.267 5.241 0    13.881 0.002 1.546 0.031 0.003 118 64.404 13.327 5.188 0    13.794 0.002 1.274 0.031 0.003 119 64.357 13.297 5.173 0    13.835 0.002 1.898 0.035 0.003 120 64.201 13.274 5.298 0    13.902 0.001 1.805 0.033 0.003 121 64.248 13.267 5.282 0    13.902 0.002 1.693 0.032 0.003 122 66.710 11.880 6.750 4.420 6.790 0.480 1.570 0    0    123 63.908 13.579 5.355 0    13.784 0.018 1.554 0.032 0.038 124 63.904 13.557 5.364 0    13.784 0.019 1.553 0.032 0.042 125 63.829 13.526 5.371 0    13.849 0.019 1.551 0.032 0.042 126 63.753 13.496 5.378 0    13.915 0.019 1.550 0.031 0.042 127 63.866 13.506 5.384 0    13.826 0.020 1.534 0.031 0.039 128 63.831 13.525 5.386 0    13.805 0.019 1.531 0.047 0.042 129 63.829 13.530 5.410 0    13.819 0.018 1.502 0.035 0.038 130 63.885 13.430 5.404 0    13.849 0.017 1.524 0.032 0.040 131 63.849 13.467 5.403 0    13.853 0.017 1.522 0.031 0.038 132 63.850 13.443 5.406 0    13.858 0.019 1.525 0.030 0.038 133 63.811 13.396 5.406 0    13.960 0.018 1.523 0.030 0.036 134 63.967 13.447 5.350 0    13.794 0.018 1.515 0.031 0.043 135 63.899 13.458 5.373 0    13.838 0.019 1.518 0.030 0.041 136 63.833 13.374 5.393 0    13.981 0.018 1.515 0.031 0.036 137 63.862 13.366 5.413 0    13.940 0.019 1.524 0.032 0.035 138 63.889 13.339 5.443 0    13.936 0.019 1.511 0.030 0.034 139 63.966 13.317 5.416 0    13.920 0.019 1.501 0.031 0.030 140 63.785 13.536 5.400 0    13.887 0.017 1.593 0.032 0.029 141 63.605 13.755 5.385 0    13.854 0.016 1.684 0.032 0.028 142 63.483 13.863 5.368 0    13.865 0.017 1.736 0.032 0.030 143 63.577 13.911 5.335 0    13.767 0.016 1.758 0.032 0.031 144 63.420 13.908 5.329 0    13.688 0.017 1.770 0.035 0.032 145 63.533 13.952 5.327 0    13.749 0.016 1.776 0.035 0.032 146 63.606 13.962 5.327 0    13.701 0.016 1.764 0.032 0.030 147 63.534 13.971 5.321 0    13.775 0.016 1.769 0.033 0.031 148 63.497 13.981 5.325 0    13.806 0.016 1.773 0.034 0.026 149 63.586 13.935 5.327 0    13.766 0.016 1.765 0.036 0.026 150 63.760 13.990 5.018 0    13.801 0.016 1.800 0.040 0.025 151 64.329 13.726 4.690 0    13.648 0.130 1.747 0.043 0.025 152 64.970 13.353 4.349 0    13.452 0.299 1.708 0.040 0.026 153 65.667 12.945 4.009 0    13.242 0.463 1.662 0.035 0.023 154 65.642 12.929 3.999 0    13.182 0.516 1.669 0.032 0.027 155 65.761 12.858 3.984 0    13.162 0.520 1.655 0.033 0.027 156 65.810 12.813 3.976 0    13.157 0.531 1.650 0.033 0.027 157 65.829 12.819 3.959 0.000 13.147 0.535 1.641 0.035 0.027 158 65.852 12.778 3.948 0.000 13.172 0.536 1.651 0.036 0.027 159 65.632 12.722 4.275 0.000 13.126 0.539 1.639 0.038 0.026 160 65.482 12.643 4.594 0.000 13.047 0.538 1.631 0.043 0.027 161 65.466 12.564 4.906 0.674 12.257 0.531 1.616 0.045 0.026 162 65.913 12.426 5.228 1.344 11.060 0.520 1.630 0.046 0.026 163 66.291 12.297 5.546 2.108 9.874 0.510 1.616 0.048 0.025 164 66.613 12.136 5.844 2.989 8.674 0.500 1.600 0.045 0.025 165 67.438 12.081 6.103 3.371 7.370 0.490 1.606 0.045 0.026 166 66.985 11.938 6.296 4.355 6.861 0.483 1.590 0.044 0.024 167 66.954 11.921 6.410 4.362 6.802 0.481 1.587 0.043 0.023 168 66.924 11.903 6.523 4.369 6.743 0.480 1.584 0.043 0.022 169 66.822 11.886 6.636 4.403 6.726 0.480 1.577 0.041 0.022 170 66.720 11.868 6.749 4.437 6.709 0.479 1.570 0.040 0.021 TiO₂/ Ex. ZrO₂ TiO₂ Fe₂O₃ MnO CoO Total R₂O—Al₂O₃ R_(x)O—Al₂O₃ Fe₂O₃ 116 0.000 0.734 0.505 0 0 100 0.556 2.632 1.452 117 0.000 1.217 0.506 0 0 100 0.616 2.193 2.407 118 0.000 1.470 0.506 0 0 100 0.470 1.775 2.905 119 0.000 1.079 0.322 0 0 100 0.540 2.473 3.353 120 0.000 0.980 0.503 0 0 100 0.630 2.469 1.950 121 0.000 0.882 0.689 0 0 100 0.637 2.362 1.280 122 0    0.880 0.520 0 0 100 −0.190 1.380 1.692 123 0.009 1.183 0.519 0 0 100 0.223 1.809 2.278 124 0.009 1.192 0.525 0 0 100 0.246 1.831 2.271 125 0.010 1.218 0.534 0 0 100 0.342 1.925 2.281 126 0.011 1.244 0.543 0 0 100 0.438 2.019 2.291 127 0.010 1.227 0.538 0 0 100 0.339 1.905 2.282 128 0.012 1.242 0.541 0 0 100 0.298 1.876 2.295 129 0.013 1.243 0.543 0 0 100 0.307 1.844 2.290 130 0.012 1.242 0.545 0 0 100 0.436 1.993 2.277 131 0.012 1.242 0.547 0 0 100 0.403 1.956 2.270 132 0.013 1.251 0.548 0 0 100 0.433 1.988 2.284 133 0.011 1.243 0.547 0 0 100 0.582 2.134 2.272 134 0.015 1.252 0.548 0 0 100 0.365 1.911 2.284 135 0.015 1.243 0.546 0 0 100 0.399 1.948 2.275 136 0.013 1.242 0.546 0 0 100 0.625 2.171 2.275 137 0.013 1.233 0.543 0 0 100 0.593 2.150 2.271 138 0.013 1.225 0.542 0 0 100 0.616 2.157 2.262 139 0.012 1.226 0.544 0 0 100 0.621 2.154 2.255 140 0.012 1.142 0.548 0 0 100 0.368 1.993 2.084 141 0.011 1.058 0.552 0 0 100 0.115 1.832 1.915 142 0.013 1.018 0.557 0 0 100 0.019 1.787 1.829 143 0.011 0.983 0.558 0 0 100 −0.128 1.662 1.761 144 0.013 1.210 0.561 0 0 100 −0.203 1.602 2.157 145 0.011 0.991 0.558 0 0 100 −0.186 1.625 1.776 146 0.012 0.974 0.558 0 0 100 −0.245 1.551 1.747 147 0.008 0.965 0.558 0 0 100 −0.180 1.622 1.729 148 0.007 0.958 0.559 0 0 100 −0.159 1.647 1.713 149 0.007 0.959 0.558 0 0 100 −0.153 1.648 1.717 150 0.007 0.962 0.562 0 0 100 −0.173 1.666 1.711 151 0.008 1.046 0.589 0 0 100 0.051 1.842 1.777 152 0.009 1.152 0.623 0 0 100 0.398 2.146 1.848 153 0.009 1.265 0.661 0 0 100 0.759 2.456 1.913 154 0.011 1.299 0.676 0 0 100 0.769 2.471 1.922 155 0.010 1.298 0.673 0 0 100 0.824 2.512 1.928 156 0.010 1.299 0.674 0 0 100 0.875 2.558 1.928 157 0.010 1.305 0.673 0 0 100 0.863 2.538 1.939 158 0.010 1.297 0.673 0 0 100 0.931 2.618 1.928 159 0.010 1.301 0.672 0 0 100 0.944 2.621 1.938 160 0.012 1.295 0.669 0 0 100 0.942 2.616 1.937 161 0.011 1.239 0.647 0 0 100 0.898 2.559 1.914 162 0.009 1.162 0.619 0 0 100 0.497 2.173 1.878 163 0.009 1.067 0.590 0 0 100 0.195 1.860 1.808 164 0.007 0.987 0.561 0 0 100 0.027 1.672 1.759 165 0.008 0.907 0.536 0 0 100 −0.850 0.801 1.694 166 0.008 0.875 0.520 0 0 100 −0.239 1.395 1.682 167 0.008 0.870 0.519 0 0 100 −0.275 1.356 1.677 168 0.008 0.865 0.517 0 0 100 −0.310 1.317 1.671 169 0.008 0.863 0.517 0 0 100 −0.276 1.342 1.670 170 0.008 0.862 0.516 0 0 100 −0.243 1.367 1.669

TABLE X Indent Liquidus Temp (° C.)- Liquidus Temp (° C.)- LiqVisc (kP)-24 LiqVisc (kP)-72 Strain Anneal Soft a P Thres. 24 hrs. 72 hrs. hrs. hrs. Ex. Pt. ° C. Pt. ° C. Pt. ° C. (10⁻⁷/° C.) (g/cm³) β-OH (kgf) Air Int. Pt. Air Int. Pt. Air Int. Pt. Air Int. Pt. 116 553 602 865 75.5 2.413 985 1000 1000 117 550 601 869 76 2.413 15-20 990 995 990 1782 1585 1782 118 554 605 883 75.4 2.412 1085 1070 1070 257 344 344 119 555 604 861 75.8 2.41  990 995 990 120 552 603 863 77.2 2.414 1000 1000 995 121 551 602 859 76.6 2.417 1025 1035 1040 739 597 538 122 509 554 812 60.4 2.369 1015 1030 1020 320 239 290 123 558 608 879.4 75 2.406 0.496 1040 1050 1050 568 463 463 124 125 126 2.407 127 128 556 607 2.406 0.471 129 1065 1065 1065 330 330 330 130 1050 1050 1055 425 425 384 131 132 133 1050 1055 1055 439 396 396 134 557 608 2.406 0.465 1075 1065 1070 295 362 327 135 136 2.407 1055 1055 1050 388 388 431 137 138 553 603 867.1 75.1 2.407 0.476 139 140 1045 1055 1050 497 406 449 141 2.408 1025 1040 1040 870 625 625 142 143 563 614 2.408 0.458 1060 1065 1060 407 368 407 144 1070 1070 1075 326 326 295 145 146 147 148 149 561 613 2.407 0.497 150 151 2.409 1065 1060 1060 411 454 454 152 1070 1065 1065 418 462 462 153 562 614 889.3 76 2.414 0.424 154 155 2.416 1075 1070 1065 416 459 507 156 157 158 563 614 2.415 0.441 159 1075 1070 1060 373 412 503 160 161 162 1070 1070 1070 238 238 238 163 1060 1060 1065 222 222 203 164 519 567 2.383 0.498 1060 1065 1065 206 188 188 165 166 2.368 167 168 169 170 513 561 60.3 2.368 0.554 1055 1065 1045 145 122 174 HTV Ex. A B To T200 P T16 kP T35 kP T160 kP Indentation Threshold 430 116 117 −3.30734265 8945.332233 54.12027364 1649 1245 1193 1105 118 −3.943709486 10557.79007 −43.72587969 1647 1252 1200 1110 119 120 121 −3.72223712 9886.571911 −5.851457092 1636 1241 1190 1102 122 −2.953207662 8345.482028 28.31570186 1617 1194 1141 1051 123 −3.998970355 10607.22174 −47.53043617 1636 1246 1194 1105 124 125 126 127 128 129 −3.662290354 9757.207057 2.219928775 1638 1243 1191 1103 130 −3.996576605 10658.76698 −57.44735184 1635 1242 1191 1101 131 132 133 −2.838759569 7941.917342 113.6168048 1659 1241 1189 1101 134 −2.735780569 7667.308512 140.612092 1663 1245 1194 1106 135 136 −2.93989907 8155.890629 98.77631831 1655 1240 1189 1100 137 138 139 140 −3.885449585 10279.76775 −27.81773689 1634 1243 1192 1103 141 −3.164251035 8524.185247 88.64381053 1648 1246 1194 1107 142 143 −4.025680139 10506.38682 −30.3745192 1630 1246 1196 1108 144 −3.893817967 10158.71538 −9.860563075 1630 1245 1194 1107 145 146 147 148 149 150 151 −4.070974917 10734.94875 −43.47341758 1641 1254 1203 1114 152 −3.982037548 10674.56709 −41.58276344 1657 1262 1210 1120 153 154 155 −3.822080075 10411.01967 −27.74613813 1673 1269 1217 1126 156 157 158 159 −3.435473834 9488.852121 21.51967142 1676 1264 1211 1120 160 161 162 −3.715779117 10364.57238 −69.94158823 1653 1239 1185 1092 163 −3.774518631 10532.60088 −94.74870613 1639 1225 1171 1078 164 −3.676116288 10214.74357 −76.20201457 1633 1220 1166 1074 165 166 167 168 169 170 −3.673843809 10131.86317 −91.71249262 1604.03264 1194.389277 1141.187464 1049.524779 Color L D65 SCE L* Ex. As-made T_(n) 620° C. T_(n) 630° C. T_(n) 640° C. T_(n) 660° C. 675-4 700-4 725-4 750-4 775-4 800-4 116 117 1.26 3.53 4.73 23.76 118 0.44 0.62 0.94 1.52 119 120 121 20.8 7.27 12.11 15.69 122 123 0.6 13.13 124 0.27 3.42 125 0.57 5.07 126 0.34 6.35 127 128 129 130 131 132 133 134 135 136 137 138 139 140 0.36 7.63 141 0.38 6.59 142 143 0.57 5.6 144 0.23 2.12 145 146 147 148 149 150 151 0.2 2.85 152 0.46 1.76 153 154 155 0.3 0.98 156 157 158 159 0.41 2.66 160 161 0.53 0.34 162 0.14 0.17 0.22 0.205 1.93 163 0.41 0.19 0.2 0.205 3 164 0.24 0.7 165 166 167 0.27 0.72 0.69 1.51 168 0.38 1.2 0.86 1.52 169 0.28 0.71 0.67 1.43 170 0.51 0.76 1.13 2.14 3.28 13.82 Color a D65 SCE a* Ex. As-made T_(n) 620° C. T_(n) 630° C. T_(n) 640° C. T_(n) 660° C. 675-4 700-4 725-4 750-4 775-4 800-4 116 117 0.15 −0.11 −0.49 −1.88 118 0.09 0.05 0.01 0.08 119 120 121 12.86 −0.14 −0.05 −0.4 122 123 −0.03 −0.99 124 0.01 −0.14 125 0.03 −0.28 126 0.06 −0.67 127 128 129 130 131 132 133 134 135 136 137 138 139 140 −0.01 −0.5 141 −0.06 −0.45 142 143 0.01 −0.29 144 −0.01 −0.1 145 146 147 148 149 150 151 0 0.08 152 −0.08 −0.15 153 154 155 0 −0.01 156 157 158 159 −0.11 −0.1 160 161 0.35 0.7 162 0 −0.03 −0.07 −0.05 −0.14 163 −0.05 −0.13 −0.1 −0.04 −0.16 164 −0.04 −0.09 165 166 167 −0.03 0 −0.01 −0.08 168 0.04 −0.02 0 −0.15 169 0.07 −0.05 −0.02 −0.09 170 −0.1 −0.01 −0.03 3.41 −0.03 −0.69 Color b D65 SCE b* Ex. As-made T_(n) 620° C. T_(n) 630° C. T_(n) 640° C. T_(n) 660° C. 675-4 700-4 725-4 750-4 775-4 800-4 116 117 −1.34 −4.65 −5.72 −3.94 118 −0.28 −0.63 −1.42 −2.33 119 120 121 25.58 −3.97 −3.45 −3.34 122 123 −1.04 −7.5 124 −0.78 −4.28 125 −1.1 −5.9 126 −0.73 −6.25 127 128 129 130 131 132 133 134 135 136 137 138 139 140 −0.63 −3.62 141 −0.36 −3.44 142 143 −0.36 −2.93 144 −0.43 −2.96 145 146 147 148 149 150 151 −0.18 −2.19 152 −0.25 −1.87 153 154 155 −0.29 −1.32 156 157 158 159 −0.31 −2.86 160 161 −0.27 −0.03 162 −0.36 −0.36 0.07 −0.1 −2.48 163 −0.42 −0.09 0.02 −0.15 −3.05 164 −0.11 −1.02 165 166 167 −0.48 −0.6 −0.72 −0.81 168 −0.32 −0.85 −0.93 −0.84 169 −0.45 −0.66 −0.81 −0.85 170 −0.53 −0.78 −0.87 1.03 −1.6 −0.47

Accordingly, various modifications, adaptations, and alternatives may occur to one skilled in the art without departing from the spirit and scope of this disclosure. It should be understood that all such modifications and improvements have been deleted herein for the sake of conciseness and readability but are properly within the scope of the following claims. 

1-14. (canceled)
 15. A glass-ceramic comprising: greater than 0 wt % and less than about 20 wt % of one or more crystalline phases, and a compressive stress of at least about 200 MPa and a depth of layer of at least about 15 μm, wherein at least one crystalline phase comprises a plurality of crystallites in the Fe₂O₃—TiO₂—MgO system.
 16. The glass-ceramic of claim 15, wherein the glass ceramic exhibits any one of: an average edge strength, as measured by 4—point bend of at least about 700 MPa, an average flexural strength, as measured by ring-on-ring testing, of about 2000 N or greater, and an average flexural strength, as measured by abraded ring-on-ring testing, of about 1000 N or greater. 17-21. (canceled)
 22. The glass-ceramic of claim 15, wherein the glass ceramic exhibits an average edge strength, as measured by 4-point bend of at least about 700 MPa.
 23. The glass-ceramic of claim 15, wherein the glass ceramic exhibits an average flexural strength, as measured by ring-on-ring testing, of about 2000 N or greater
 24. The glass-ceramic of claim 15, wherein the glass ceramic exhibits an average flexural strength, as measured by abraded ring-on-ring testing, of about 1000 N or greater.
 25. The glass-ceramic of claim 15, wherein the crystallites comprise at least one of: MgO in an amount in the range from about 5 mol % to about 50 mol %, Fe₂O₃ in an amount in the range from about 15 mol % to about 65 mol %, and TiO₂ in an amount in the range from about 25 mol % to about 45 mol %.
 26. The glass-ceramic of claim 15, wherein the crystallites comprise MgO in an amount in the range from about 5 mol % to about 50 mol %.
 27. The glass-ceramic of claim 15, wherein the crystallites comprise Fe₂O₃ in an amount in the range from about 15 mol % to about 65 mol %.
 28. The glass-ceramic of claim 15, wherein the crystallites comprise TiO₂ in an amount in the range from about 25 mol % to about 45 mol %.
 29. The glass-ceramic of claim 15, wherein the glass-ceramic comprises a color presented in CIELAB color space coordinates for CIE illuminant D65 determined from reflectance spectra measurements using a spectrophotometer with SCE of the following ranges: L*=from about 14 to about 30; a*=from about −1 to about +3; and b*=from about −7 to about +3.
 30. The glass-ceramic of claim 15, wherein the plurality of crystallites form an area fraction of about 15% or less.
 31. The glass-ceramic of claim 15, wherein the crystallites comprise at least one of magnetite, pseudobrookite, or ϵ-Fe₂O₃.
 32. The glass-ceramic of claim 15, wherein the one or more crystalline phases comprises one or more ϵ-Fe₂O₃ crystallites.
 33. The glass-ceramic of claim 15, wherein the one or more crystalline phases comprises a solid solution of ϵ-Fe₂O₃ and MgTiO₃.
 34. The glass-ceramic of claim 15, wherein the one or more crystalline phases comprises a solid solution of MgO, TiO₂, and Fe₂O₃.
 35. The glass-ceramic of claim 15, wherein the ratio of TiO₂:Fe₂O₃ is in the range from about 0.1 to about
 3. 36. The glass-ceramic of claim 15, comprising, on an oxide basis, in mol %: SiO₂ in the range from about 50 to about 76; Al₂O₃ in the range from about 4 to about 25; P₂O₅+B₂O₃ in the range from about 0 to about 14; Fe₂O₃ in the range from about 0.25 to about 5; R₂O in the range from about 2 to about 20, wherein R₂O includes one or more of Li₂O, Na₂O, K₂O, Rb₂O, Cs₂O, Cu₂O, and Ag₂O; one or more nucleating agents in the range from about 0 to about 5; RO in the range from about 0 to about 20, wherein RO includes one or more of MgO, CaO, SrO, BaO, and ZnO; and at least one of the compositional relationships of: R₂O—Al₂O₃ in the range from about −2 to about 3; and R₂O+RO—Al₂O₃ in the range from about −2 to about 5, wherein the crystalline phases comprise a plurality of crystallites in the Fe₂O₃—TiO₂—MgO system and having an area fraction of about 10% or less.
 37. The glass-ceramic of claim 36, wherein the one or more nucleating agents comprises TiO₂.
 38. The glass-ceramic of claim 36, wherein the composition comprises, on an oxide basis, in mol %: SiO₂ in an amount in the range from about 58 to about 72; Al₂O₃ in an amount in the range from about 8 to about 20; B₂O₃ in an amount in the range from about 0 to about 12; R₂O in an amount in the range from about 2 to about 20; RO in an amount in the range from about 0 to about 10; SnO₂ in an amount in the range from about 0 to about 0.5; TiO₂ in an amount in the range from about 0.25 to about 5; Fe₂O₃ in an amount in the range from about 0.25 to about 5; and at least one of the compositional relationships of: R₂O—Al₂O₃ in the range from about −2 to about 3; and R₂O+RO—Al₂O₃ in the range from about −2 to about
 5. 39. An electronic device comprising the glass-ceramic of claim
 15. 40. A light emitting device comprising a display cover, wherein the display cover comprises the glass-ceramic of claim
 15. 